Polyethylene compositions having high dimensional stability and excellent processability for caps and closures

ABSTRACT

A dual reactor solution polymerization process gives high density polyethylene compositions containing a first ethylene copolymer and a second ethylene copolymer and which have high dimensional stability, excellent processability as well as good organoleptic properties and reasonable stress cracking resistance. The polyethylene compositions are suitable for compression molding or injection molding applications and are useful, for example, in the manufacture of caps and closures for bottles, and for example, in bottles containing non-pressurized liquids.

This application is a continuation-in-part of U.S. application Ser. No. 14/098,634, filed on Dec. 6, 2013, which claims priority to and the benefit of Canadian Application No. 2,798,854, filed Dec. 14, 2012.

The present invention relates to polyethylene compositions that are useful in the manufacture of molded articles such as closures for bottles.

Polymer compositions useful for molding applications, for example, the manufacture of caps and closures for bottles are well known. Screw closures for example, are typically made from polypropylene (PP) in order to achieve the necessary cap strength, however, an inner liner composed of a soft polymer is required to provide necessary seal properties. Also a PP closure alone does not have good organoleptic properties, which is another reason to use a liner. The soft inner liner can be made from ethylene/vinyl acetate (EVA), polyvinyl chloride (PVC), butyl rubber or other suitable material. The two-part cap is costly, and single part constructions may reduce costs.

One-piece closures, such as screw caps, have more recently been made from polyethylene (PE) resins. To date the use of high density resin is required if the closures are to have sufficient stiffness, while good flow properties combined with an ability to resist cracking over time (as measured by for example, environmental stress crack resistance (ESCR)) is also desirable. Further, closures should be rapidly produced while not suffering from anisotropic shrinkage when released from a mold. Such closures, for example, screw cap closures for water and other drink bottles, should, even when produced in high turnover, consistently satisfy strict dimensional tolerances to provide a consistent fit and seal and to maintain product integrity. Polyethylene closures alone have better organoleptic properties than PP closures alone.

Polyethylene blends produced with conventional Ziegler-Natta or Phillips type catalysts systems can be made having suitably high density and ESCR properties, see for example, WO 00/71615 and U.S. Pat. No. 5,981,664. However, the use of conventional catalyst systems may produce significant amounts of low molecular weight polymer chains having high comonomer contents, which results in resins having non-ideal organoleptic properties.

Examples of high density multimodal polyethylene blends made using conventional catalyst systems for the manufacture of caps or closures are taught in U.S. Pat. Nos. 7,750,083; 7,750,082; 7,790,826; 8,044,160; and 8,129,472; U.S. Patent Applications 2007/0213468 and 2008/0287608, as well as, WO 2007/060007 and EP 2,017,302A1. Further high density, multimodal polyethylene blends made by employing conventional Ziegler-Natta catalysts are disclosed in U.S. Patent Applications 2009/0198018; 2009/0203848; 2008/0221273; 2010/0084363 and 2012/0022214.

In contrast to traditional catalysts, the use of so called single site catalysts (such as “metallocene” and “constrained geometry” catalysts) provides resin having lower catalyst residues and improved organoleptic properties as taught by U.S. Pat. No. 6,806,338. The disclosed resins are suitable for use in molded articles. Further resins comprising metallocene catalyzed components which are useful for molding applications are described in U.S. Pat. Nos. 7,022,770; 7,307,126; 7,396,878; 7,396,881; and 7,700,708.

A monomodal polyethylene composition which is useful in the preparation of a screw closure has been made using a mixed metallocene catalyst system as described in U.S. Pat. No. 8,039,569.

U.S. Patent Application 2011/0165357A1 discloses a blend of metallocene catalyzed resins which is suitable for use in pressure resistant pipe applications.

U.S. Patent Application 2006/0241256A1 teaches blends formulated from polyethylenes made using a hafnocene catalyst in the slurry phase.

A bimodal resin having a relatively narrow molecular weight distribution and long chain branching is described in U.S. Pat. No. 7,868,106. The resin is made using a bis-indenyl type metallocene catalyst in a dual slurry loop polymerization process and can be used to manufacture caps and closures.

U.S. Pat. No. 6,642,313 discloses multimodal polyethylene resins which are suitable for use in the manufacture of pipes. A dual reactor solution polymerization process is used to prepare the resins in the presence of a phosphinimine catalyst.

Narrow molecular weight distribution polyethylene blends comprising a metallocene produced polyethylene component and a Zielger-Natta or metallocene produced polyethylene component are reported in U.S. Pat. No. 7,250,474. The blends can be used in blow molding and injection molding applications such as for example, milk bottles and bottle caps respectively.

For further references describing relevant polyethylene compositions see: U.S. Pat. Nos. 7,875,690; 6,545,093; 8,129,489; 6,063,871; 5,382,630; 5,382,631; 7,928,051; 6,809,154; 7,592,395; 6,194,520; 5,858,491; 6,946,521; and 5,494,965 as well as U.S. Patent Application 2010/0121006 and 2011/0136983.

In U.S. Pat. No. 8,022,143 we disclosed a resin composition having a good balance of toughness, ESCR, processability, and organoleptic properties for use in the manufacture of caps and closures. The resins were made using a single site catalyst system in a dual reactor solution polymerization process, to provide bimodal polyethylene compositions in which comonomer was present in both a high and a low molecular weight component. The disclosed resins had a normal comonomer distribution in that the low molecular weight component had a larger amount of comonomer than did the high molecular weight component.

In CA Patent Application 2,752,407 we disclosed resins having improved ESCR, good organoleptic properties, balanced rheological and mechanical properties and which were suitable for use in the manufacture of molded articles such as closures for bottles.

One embodiment of this invention provides single-site catalyzed dual-reactor resin composition which has high dimensional stability, excellent processability and organoleptic properties as well as reasonable stress cracking resistance. The new compositions have a better isotropic shrinkage ratio (i.e. one which is closer to unity), a lower shrinkage differential between TD and MD directions (i.e. closer to zero) and better processability in the extrusion shear rate range (i.e. lower melt viscosity) compared to the resins disclosed in U.S. Pat. No. 8,022,143 and CA Patent Application 2,752,407. The present resins are especially suitable for use in the manufacture of caps and closures for bottles containing water or other non-carbonated beverages.

One embodiment of this invention provides a polyethylene composition that can be used in the manufacture of caps and closures for bottles.

One embodiment of this invention provides resins for use in the manufacture of caps and closures for bottles containing water or other non-carbonated beverages.

One embodiment of this invention provides a polyethylene composition which has good dimensional stability while maintaining low shear viscosity values at high shear rates which is desirable for high-speed injection applications.

One embodiment of this invention provides caps and closures comprising a polyethylene composition made by a two reactor solution phase polymerization process and a single site catalyst. Molded disks made from the polyethylene compositions have good dimensional stability.

One embodiment of this invention is a closure for bottles, the closure comprising a polyethylene composition, the polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs; and

wherein the closure is a hinged closure.

One embodiment of this invention provides a closure for bottles, the closure comprising a polyethylene composition, the polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs.

In an embodiment of the invention, the closure is made by compression molding.

In an embodiment of the invention, the closure is made by injection molding.

In an embodiment of the invention, the closure is a screw cap.

In an embodiment of the invention, the closure is a hinged closure.

One embodiment of this invention provides a polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.5; a composition distribution breadth index (CDBI(50)) of greater than 65%; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.5; a composition distribution breadth index (CDBI(50)) of greater than about 65%; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs.

One embodiment of this invention provides a polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.5; and a density of from 0.930 to 0.960 g/cm³; and

(2) 9 about 0 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 2.5; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(z), of less than 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs.

In an embodiment of the invention, the polyethylene composition has an ESCR Condition B (100% IGEPAL) of from about 3.5 to about 15 hrs.

In an embodiment of the invention, the polyethylene composition has a TD/MD shrinkage ratio of from about 0.90 to about 1.15 when measured according to the Dimensional Stability Test (DST).

In an embodiment of the invention, the polyethylene composition has a melt index I₂, of greater than 5.0 to less than 20 g/10 min.

In an embodiment of the invention, the first and second ethylene copolymers are made by polymerizing ethylene and an alpha olefin in the presence of a single site catalyst.

In an embodiment of the invention, the density of the second ethylene copolymer is less than 0.030 g/cm³ higher than the density of the first ethylene copolymer.

In an embodiment of the invention, the first ethylene copolymer has a melt index I₂, of from 0.1 to 3.0 g/10 min.

In an embodiment of the invention, the second ethylene copolymer has a melt index I₂, of from 100 to 5000 g/10 min.

In an embodiment of the invention, the polyethylene composition has a melt index I₂, of from 6 to 12 g/10 min.

In an embodiment of the invention, the polyethylene composition has a bimodal molecular weight distribution as determined by gel permeation chromatography.

In an embodiment of the invention, the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is at least 1.5.

In an embodiment of the invention, the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.5 to 6.

In an embodiment of the invention, the first ethylene copolymer has a density of from 0.936 to 0.952 g/cm³.

In an embodiment of the invention, the second ethylene copolymer has a density of less than 0.965 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density of from 0.952 to 0.960 g/cm³.

In an embodiment of the invention, the polyethylene composition has no long chain branching.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI(50)) of greater than about 65%.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI(50)) of greater than about 70%.

In an embodiment of the invention, the first and second ethylene copolymers each have a composition distribution breadth index (CDBI(50)) of greater than about 65%.

In an embodiment of the invention, the polyethylene composition comprises: from 25 to 60 wt % of the first ethylene copolymer; and from 75 to 40 wt % of the second ethylene copolymer.

In an embodiment of the invention, the polyethylene composition has a comonomer content of less than about 0.5 mol % as determined by ¹³C NMR.

In an embodiment of the invention, the polyethylene composition further comprises a nucleating agent.

In an embodiment of the invention, the first and second ethylene copolymers are copolymers of ethylene and 1-octene.

One embodiment of this invention provides a process to prepare a polyethylene composition, the polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index 1₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs.; the process comprising contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the invention, the at least two polymerization reactors comprise a first reactor and a second reactor configured in series.

In an embodiment of the invention, the at least one alpha-olefin is fed exclusively to the first reactor.

One embodiment of the invention is a process for preparing a closure for bottles wherein the process comprises at least one compression molding or injection molding step and wherein the closure comprises a polyethylene composition, the polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³;

wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs; and

wherein the closure is a hinged closure.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 shows the balance of processability and ESCR for various inventive resins of the present invention and for some comparative resins as demonstrated by a plot of the processability indicator (100/η at 10⁵ s⁻¹ and 240° C.) against the ESCR B100. The inventive resins may be used in caps and closures manufacture.

FIG. 2 shows the balance of processability and impact strength for various inventive resins of the present invention and for some comparative resins as demonstrated by a plot of the Notched Izod Impact Strength (J/m) against the processability indicator (100/η at 10⁵ s⁻¹ and 240° C.). The inventive resins may be used for application in caps and closures manufacture.

FIG. 3 shows a graph of the dimensional stability of various inventive resins of the present invention and for some comparative resins, where dimensional stability is demonstrated by a plot of the TD/MD shrinkage ratio (for an injection molded disk of circular shape) against post-molding time (in hours).

FIGS. 4A and 4B show the TREF profile of an inventive resin (4A) and a comparative resin (4B) where each is made with a single site catalyst by solution polymerization. The inventive resin (4A) has a CDBI(50) of greater than about 70 wt % and may be used in the manufacture of caps and closures. The comparative resin (4B) has a CDBI(50) of less than about 50 wt %.

The present disclosure is related to caps and closures for bottles and to the polyethylene compositions and processes used to manufacture them. The polyethylene compositions are composed of at least two ethylene copolymer components: a first ethylene copolymer and a second ethylene copolymer. The polyethylene compositions of the invention have good dimensional stability and are ideal materials for use in manufacturing caps and closures for bottles containing non-carbonated soft drinks.

Notwithstanding that the numerical ranges and parameters setting forth the broad scope of the invention are approximations, the numerical values set forth in the specific examples are reported as precisely as possible. Any numerical values, however, inherently contain certain errors necessarily resulting from the standard deviation found in their respective testing measurements.

Also, it should be understood that any numerical range recited herein is intended to include all sub-ranges subsumed therein. For example, a range of “1 to 10” is intended to include all sub-ranges between and including the recited minimum value of 1 and the recited maximum value of 10; that is, having a minimum value equal to or greater than 1 and a maximum value of equal to or less than 10. Because the disclosed numerical ranges are continuous, they include every value between the minimum and maximum values. Unless expressly indicated otherwise, the various numerical ranges specified in this application are approximations.

All compositional ranges expressed herein are limited in total to and do not exceed 100 percent (volume percent or weight percent) in practice. Where multiple components can be present in a composition, the sum of the maximum amounts of each component can exceed 100 percent, with the understanding that, and as those skilled in the art readily understand, that the amounts of the components actually used will conform to the maximum of 100 percent.

The terms “cap” and “closure” are used interchangeably in the current invention, and both connote any suitably shaped molded article for enclosing, sealing, closing or covering etc., a suitably shaped opening, a suitably molded aperture, an open necked structure or the like used in combination with a container, a bottle, a jar and the like.

It is well known that metallocene catalysts and other so called “single site catalysts” generally incorporate comonomer more evenly than traditional Ziegler-Natta catalysts when used for catalytic ethylene copolymerization with alpha olefins. This fact is often demonstrated by measuring the composition distribution breadth index (CDBI) for corresponding ethylene copolymers. The composition distribution of a polymer can be characterized by the short chain distribution index (SCDI) or composition distribution breadth index (CDBI). The definition of composition distribution breadth index (CDBI(50)) can be found in PCT publication WO 93/03093 and U.S. Pat. No. 5,206,075. The CDBI(50) is conveniently determined using techniques which isolate polymer fractions based on their solubility (and hence their comonomer content). For example, temperature rising elution fractionation (TREF) as described by Wild et al. J. Poly. Sci., Poly. Phys. Ed. Vol. 20, p441, 1982 or in U.S. Pat. No. 4,798,081 can be employed. From the weight fraction versus composition distribution curve, the CDBI(50) is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 50% of the median comonomer content on each side of the median. Alternatively, the CDBI(25), which is sometimes used in the art, is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 25% of the median comonomer content on each side of the median.

The First Ethylene Copolymer

The first ethylene copolymer of the polyethylene composition of the current invention has a density of from about 0.930 g/cm³ to about 0.960 g/cm³; a melt index, I₂, of more than 0.1 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 3.0 and a weight average molecular weight M_(w), that is greater than the M_(w) of the second ethylene copolymer. In one embodiment, the weight average molecular weight M_(w), of the first ethylene copolymer is at least 50,000 g/mol.

By the term “ethylene copolymer” it is meant that the copolymer comprises both polymerized ethylene and at least one polymerized alpha-olefin comonomer, with polymerized ethylene being the majority species.

In an embodiment of the invention, the first ethylene copolymer is made with a single site catalyst, such as, for example, a phosphinimine catalyst.

The comonomer (i.e., alpha-olefin) content in the first ethylene copolymer can be from about 0.05 to about 3.0 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods, or as calculated from a reactor model (see the Examples section). The comonomer is one or more suitable alpha olefin, which include, but are not limited to, 1-butene, 1-hexene, 1-octene and the like. In one embodiment the alpha olefin is 1-octene.

The short chain branching in the first ethylene copolymer can be from about 0.25 to about 15 short chain branches per thousand carbon atoms (SCB1/1000Cs). In further embodiments of the invention, the short chain branching in the first ethylene copolymer can be from 0.25 to 10, or from 0.25 to 7.5, or from 0.25 to 5, or from 0.25 to 3 branches per thousand carbon atoms (SCB1/1000Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc. The comonomer is one or more suitable alpha-olefin, which include, but are not limited to, 1-butene, 1-hexene, 1-octene and the like. In one embodiment the alpha olefin is 1-octene.

In an embodiment of the invention, the comonomer content in the first ethylene copolymer is greater than comonomer content of the second ethylene copolymer (as reported, for example, in mol %).

In an embodiment of the invention, the amount of short chain branching in the first ethylene copolymer is greater than the amount of short chain branching in the second ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000Cs).

In some embodiments of the invention the melt index, I₂, of the first ethylene copolymer can be from 0.1 to 10 g/10 min and including narrower ranges within this range and any numbers encompassed by these ranges. For example, the melt index I₂ of the first ethylene composition can be from above 0.1 to below 10 g/10 min, or can be from 0.1 to 7.5 g/10 min, or from 0.1 to 5.0 g/10 min, or from 0.1 to 3.0 g/10 min, or from 0.1 to 2.5 g/10 min, or from 0.1 to 1.0 g/10 min.

In an embodiment of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 50,000 to about 225,000 g/mol including narrower ranges and any numbers encompassed by these ranges. For example, in another embodiment of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 75,000 to about 200,000. In further embodiments of the invention, the first ethylene copolymer has a weight average molecular weight M_(w) of from about 75,000 to about 175,000, or from about 85,000 to about 150,000, or from about 100,000 to about 150,000.

The density of the first ethylene copolymer is in the present invention from 0.930 to 0.960 g/cm³ or can be a narrower range within this range and any numbers encompassed by these ranges. For example, in further embodiments of the invention, the density of the first ethylene copolymer can be from 0.936 to 0.960 g/cm³, or can be from 0.938 to 0.960 g/cm³, or from 0.936 to 0.952 g/cm³, or from 0.938 to 0.952 g/cm³, or from 0.936 to 0.950 g/cm³, or from 0.938 to 0.950 g/cm³, or from 0.936 to 0.947 g/cm³, or from 0.938 to 0.947 g/cm³, or from 0.936 to 0.945 g/cm³, or from 0.938 to 0.945 g/crn³.

In embodiments of the invention, the first ethylene copolymer has a molecular weight distribution M_(w)/M_(n) of <3.0, or ≦2.7, or <2.7, or ≦2.5, or <2.5, or ≦2.3, or from 0.8 to 2.3.

In an embodiment of the invention, the first ethylene copolymer of the polyethylene composition is produced with a single site catalyst and has a weight average molecular weight M_(w), of at least 50,000 g/mol; a molecular weight distribution, M_(w)/M_(n), of less than 3.0 and a density of from 0.936 to 0.950 g/cm³.

In an embodiment of the invention, a single site catalyst is used and the ethylene copolymer has a CDBI(50) of at least about 65% by weight, or at least about 70%, or at least about 75%, or at least about 80%, or at least about 85%, during solution phase polymerization in a single reactor, is used in the preparation of the first ethylene copolymer.

In an embodiment of the present invention, the first ethylene copolymer is ethylene copolymer which has a CDBI(50) of greater than about 60% by weight, or greater than about 65%, or greater than about 70%, or greater than about 75%, or greater than about 80%, or greater than about 85%.

The first ethylene copolymer can comprise from about 10 to about 70 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from 20 to about 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from about 25 to about 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from about 30 to about 60 weight percent (wt %) of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the first ethylene copolymer comprises from about 40 to about 50 weight percent (wt %) of the total weight of the first and second ethylene copolymers.

The Second Ethylene Copolymer

The second ethylene copolymer of the polyethylene composition of the current invention has a density below 0.967 g/cm³ but which is higher than the density of the first ethylene copolymer; a melt index I₂, of from about 50 to 10,000 g/10 min; a molecular weight distribution, M_(w)/M_(n), of below about 3.0 and a weight average molecular weight M_(w) that is less than the M_(w) of the first ethylene copolymer. In one embodiment, the weight average molecular weight, M_(w) of the second ethylene copolymer will be below 45,000 g/mole.

In an embodiment of the invention, the second ethylene copolymer is made with a single site catalyst, such as for example a phosphinimine catalyst.

The comonomer content in the second ethylene copolymer can be from about 0.05 to about 3 mol % as measured by ¹³C NMR, or FTIR or GPC-FTIR methods, or as calculated from a reactor model (see Examples section). The comonomer is one or more suitable alpha olefins, which include, but are not limited to, 1-butene, 1-hexene, 1-octene and the like. In one embodiment the alpha olefin is 1-octene.

The short chain branching in the second ethylene copolymer can be from about 0.25 to about 15 short chain branches per thousand carbon atoms (SCB1/1000Cs). In further embodiments of the invention, the short chain branching in the first ethylene copolymer can be from 0.25 to 10, or from 0.25 to 7.5, or from 0.25 to 5, or from 0.25 to 3 branches per thousand carbon atoms (SCB1/1000Cs). The short chain branching is the branching due to the presence of alpha-olefin comonomer in the ethylene copolymer and will for example have two carbon atoms for a 1-butene comonomer, or four carbon atoms for a 1-hexene comonomer, or six carbon atoms for a 1-octene comonomer, etc. The comonomer is one or more suitable alpha olefin. Examples of alpha olefins include, but are not limited to 1-butene, 1-hexene, 1-octene and the like. In one embodiment the alpha olefin is 1-octene.

In an embodiment of the invention, the comonomer content in the second ethylene copolymer is less than the comonomer content of the first ethylene copolymer (as reported for example in mol %).

In an embodiment of the invention, the amount of short chain branching in the second ethylene copolymer is less than the amount of short chain branching in the first ethylene copolymer (as reported in short chain branches, SCB per thousand carbons in the polymer backbone, 1000Cs).

In the present invention, the density of the second ethylene copolymer is less than 0.967 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is less than 0.966 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is less than 0.965 g/cm³. In another embodiment of the invention, the density of the second ethylene copolymer is less than 0.964 g/cm³. In an embodiment of the invention, the density of the second ethylene copolymer is from 0.952 to 0.967 g/cm³ or can be a narrower range within this range, including all the number encompassed within these ranges.

In the present invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.037 g/cm³ higher than the density of the first ethylene copolymer. In an embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.035 g/cm³ higher than the density of the first ethylene copolymer. In another embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.030 g/cm³ higher than the density of the first ethylene copolymer. In still another embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.027 g/cm³ higher than the density of the first ethylene copolymer. In still another embodiment of the invention, the second ethylene copolymer has a density which is higher than the density of the first ethylene copolymer, but less than about 0.025 g/cm³ higher than the density of the first ethylene copolymer.

In an embodiment of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of less than 45,000 g/mol. In another embodiment of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 7,500 to about 40,000. In further embodiments of the invention, the second ethylene copolymer has a weight average molecular weight M_(w) of from about 9,000 to about 35,000, or from about 10,000 to about 30,000, or from about 10,000 to 25,000.

In embodiments of the invention, the second ethylene copolymer has a molecular weight distribution (M_(w)/M_(n)) of <3.0, or ≦2.7, or <2.7, or ≦2.5, or <2.5, or ≦2.3, or from 1.8 to 2.3.

In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 50 to 10,000 g/10 min. In another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 100 to 5,000 g/10 min. In another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 50 to 3,500 g/10 min. In another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 100 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1000 to 7000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1200 to 10,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be from 1200 to 7,000 g/10 min. In yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 1200, but less than 5000 g/10 min. In still yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 1000, but less than 3000 g/10 min. In still yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 500, but less than 3000 g/10 min. In still yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 250, but less than 2700 g/10 min. In still yet another embodiment of the invention, the melt index I₂ of the second ethylene copolymer can be greater than 150, but less than 2700 g/10 min.

In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 100 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 200 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 500 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1000 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1200 g/10 min. In an embodiment of the invention, the melt index I₂ of the second ethylene copolymer is greater than 1500 g/10 min.

In an embodiment of the invention, the second ethylene copolymer of the polyethylene composition is made with a single site catalyst and has a weight average molecular weight, M_(w), of at most 45,000; a molecular weight distribution, M_(w)/M_(n), of less than 3.0 and a density higher than the density of said first ethylene copolymer, but less than 0.967 g/cm³.

In an embodiment of the invention, a single site catalyst is used and the ethylene copolymer has a CDBI(50) of at least about 65% by weight, or at least about 70%, or at least about 75%, or at least about 80%, or at least about 85%, during solution phase polymerization in a single reactor, is used in the preparation of the second ethylene copolymer.

In an embodiment of the present invention, the second ethylene copolymer has a CDBI(50) of greater than about 60% by weight, or greater than about 65%, or greater than about 70%, or greater than about 75%, or greater than about 80%, or greater than about 85%.

The second ethylene copolymer can comprise from about 90 to about 30 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from about 80 to about 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from about 75 to about 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from about 70 to about 40 wt % of the total weight of the first and second ethylene copolymers. In an embodiment of the invention, the second ethylene copolymer comprises from about 60 to about 50 wt % of the total weight of the first and second ethylene copolymers.

In embodiments of the invention, the melt index I₂ of the second ethylene copolymer is at least 50 times, or at least 100 times, or at least 1,000 times the melt index I₂ of the first ethylene copolymer.

The Polyethylene Composition

In one embodiment the polyethylene composition will contain a first ethylene copolymer and a second ethylene copolymer (as defined herein).

In some embodiments of the invention, the polyethylene composition has a unimodal, broad unimodal, bimodal or multimodal molecular weight distribution as determined by gel permeation chromatography.

In an embodiment of the invention, the polyethylene composition that comprises a first ethylene copolymer and a second ethylene copolymer (as defined above) will have a ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (i.e., SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (i.e., SCB2) of greater than 1.0 (i.e., SCB1/SCB2>1.0).

In further embodiments of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.25. In still another embodiment of the invention, the ratio of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) is at least 1.5.

In embodiments of the invention, the ratio (SCB1/SCB2) of the short chain branching in the first ethylene copolymer (SCB1) to the short chain branching in the second ethylene copolymer (SCB2) will be from greater than 1.0 to about 12.0, or from greater than 1.0 to about 10, or from greater than 1.0 to about 7.0, or from greater than 1.0 to about 5.0, or from greater than 1.0 to about 3.0.

In an embodiment of the invention, the polyethylene composition is bimodal as determined by GPC.

A bimodal or multimodal polyethylene composition can be identified by using gel permeation chromatography (GPC). A GPC chromatograph may exhibit two or more component ethylene copolymers, where the number of component ethylene copolymers corresponds to the number of discernible peaks. One or more component ethylene copolymers may also exist as a hump, shoulder or tail relative to the molecular weight distribution of the other ethylene copolymer component. By the phrase “bimodal as determined by GPC”, it is meant that in addition to a first peak, there will be a secondary peak or shoulder which represents a higher or lower molecular weight component (i.e., the molecular weight distribution, can be said to have two maxima in a molecular weight distribution curve). Alternatively, the phrase “bimodal as determined by GPC” connotes the presence of two maxima in a molecular weight distribution curve generated according to the method of ASTM D6474-99.

The polyethylene composition of the current invention has a density of greater than or equal to 0.950 g/cm³, as measured according to ASTM D792; a melt index I₂, of from about 2 to about 22 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight); a molecular weight distribution, M_(w)/M_(n), of from about 2 to about 7, a Z-average molecular weight M_(z), of less than about 300,000; a stress exponent of less than 1.40; and an ESCR Condition B at 100% Igepal of at least about 3 hours.

In embodiments of the invention, the polyethylene composition has a comonomer content of less than about 0.75 mol %, or less than about 0.70 mol %, or less than about 0.65 mol %, or less than about 0.60 mol %, or less than about 0.55 mol %, or less than about 0.50 mol % as measured by FTIR or ¹³C NMR methods, where the comonomer is one or more suitable alpha olefins, which include, but are not limited to, 1-butene, 1-hexene, 1-octene and the like. In one embodiment the alpha olefin is 1-octene.

In the present invention, the polyethylene composition has a density of at least 0.950 g/cm³. In further embodiments of the invention, the polyethylene composition has a density of >0.952 g/cm³, or >0.953 g/cm³, or >0.955 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.950 to 0.970 g/cm³. In an embodiment of the current invention, the polyethylene composition has a density in the range of 0.950 to 0.965 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.950 to 0.962 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.952 to 0.960 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.950 to 0.960 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.950 to 0.959 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.951 to 0.957 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density in the range of 0.952 to 0.957 g/cm³.

In an embodiment of the invention, the polyethylene composition has a melt index I₂, of from 2 to 22 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg weight) and including narrower ranges within this range and all numbers encompassed by these ranges. For example, in further embodiments of the invention, the polyethylene composition has a melt index I₂, of greater than 2, but less than 22 g/10 min, or from 2 to 15.0 g/10 min, or from 3 to 12.5 g/10 min, or from 4 to 12.5 g/10 min, or from greater than 4 to less than 20 g/10 min, or from 4.5 to 10 g/10 min, or from 5 to 20 g/10 min, or from greater than 5.0 to less than 20 g/10 min, or from 3 to 15.0 g/10 min, or from 6.0 to 12.0 g/10 min, or from 6.0 to about 10.0 g/10 min, or from about 5.0 to about 12.0 g/10 min, or from more than about 5.0 to less than about 10.0 g10/min.

In an embodiment of the invention, the polyethylene composition has a “medium load” melt index, I₅, of at least about 2.5 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 5 kg weight). In another embodiment of the invention, the polyethylene composition has a medium load melt index, I₅, of greater than about 5.0 g/10 min, as measured according to ASTM D1238 (when conducted at 190° C., using a 5 kg weight). In further embodiments of the invention, the polyethylene composition has a medium load melt index, I₅, of at least about 10.0 g/10 min, or at least about 4.0 g/10 min. In still further embodiments of the invention, the polyethylene composition has a medium load melt index, I₅, of from about 5.0 to about 25.0 g/10 min, or from about 5.0 to about 20.0 g/10 min, or from about 5.0 to about 17.5 g/10 min, or from about 5.0 to about 15.0 g/10 min.

In an embodiment of the invention, the polyethylene composition has a “high load” melt index I₂₁ of at least about 100 g/10 min according to ASTM D1238 (when conducted at 190° C., using a 21 kg weight). In another embodiment of the invention, the polyethylene composition has a high load melt index I₂₁, of greater than about 150 g/10 min.

In an embodiment of the invention, the polyethylene composition has a high load melt index I₂₁, of from 125 to 500 g/10 min, or from 150 to 450 g/10 min, or from 150 to 400 g/10 min.

In an embodiment of the invention, the polyethylene composition has a number average molecular weight M_(n), of below about 30,000 g/mol. In another embodiment of the invention, the polyethylene composition has a number average molecular weight M_(n), of below about 25,000 g/mol. In yet another embodiment of the invention, the polyethylene composition has a number average molecular weight M_(n), of below about 20,000 g/mol.

In the present invention, the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7 or a narrower range within this range, including all the numbers encompassed within these ranges. For example, in further embodiments of the invention, the polyethylene composition has molecular weight distribution M_(w)/M_(n), of from 3.0 to 7.0, or from 3.5 to 6.0, or from 3.5 to 5.5.

In an embodiment of the invention, the polyethylene composition has a Z-average molecular weight, M_(z), of below about 300,000 g/mole. In another embodiment of the invention, the polyethylene composition has a Z-average molecular weight, M_(z), of below about 250,000 g/mole. In yet another embodiment of the invention, the polyethylene composition has a Z-average molecular weight, M_(z), of below about 200,000 g/mole.

In embodiments of the invention, the polyethylene composition has a ratio of Z-average molecular weight to weight average molecular weight M_(Z)/M_(W), of from 2.0 to 4.0, or from 2.0 to 3.75, or from 2.25 to 3.75, or from 2.50 to 3.5.

In embodiments of the invention, the polyethylene composition has a melt flow ratio defined as I₂₁/I₂, of from about 15 to about 50, or from about 20 to 50, or from about 22 to 50, or from about 25 to 45, or from about 30 to 45, or from about 30 to 50, or from 22 to 50, or from about 22 to less than 50.

In an embodiment of the invention, the polyethylene composition has a melt flow rate defined as I₂₁/I₅, of less than 25. In another embodiment of the invention, the polyethylene composition has a melt flow rate defined as I₂₁/I₅, of less than 20. In another embodiment of the invention, the polyethylene composition has a melt flow rate defined as I₂₁/I₅, of less than 15.

In an embodiment of the invention, the polyethylene composition has a shear viscosity at about 10⁵ s⁻¹ (240° C.) of less than about 10 (Pa·s). In further embodiments of the invention, the polyethylene composition has a shear viscosity at about 10⁵ s⁻¹ (240° C.) of less than 7.5 Pa·s, or less than 6.8 Pa·s. Simultaneously, the polyethylene composition may have a shear viscosity at about 100 s⁻¹ (240° C.) of less than about 600 Pa·s, a shear viscosity at about 200 s⁻¹ (240° C.) of less than about 500 Pa·s and a shear viscosity at about 300 s⁻¹ (240° C.) of less than about 400 Pa·s.

In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than about 0.75 mol % as determined by ¹³C NMR. In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than about 0.65 mol % as determined by ¹³C NMR. In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than about 0.55 mol % as determined by ¹³C NMR. In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is less than about 0.50 mol % as determined by ¹³C NMR. In an embodiment of the invention, the polyethylene composition has at least one type of alpha-olefin that has at least 4 carbon atoms and its content is greater than about 0.20 to less than about 0.55 mol % as determined by ¹³C NMR.

In an embodiment of the invention, the shear viscosity ratio, SVR(_(100,100000)) at 240° C. of the polyethylene composition can be from about 50 to about 90, or can be from about 55 to about 90, or from about 55 to about 85, or from about 55 to about 75. The shear viscosity ratio SVR(_(100,100000)) is determined by taking the ratio of shear viscosity at shear rate of 100 s⁻¹ andshear viscosity at shear rate of 100000 s⁻¹ as measured with a capillary rheometer at constant temperature (e.g. 240° C.), and two dies with L/D ratio of 20 and diameter of 0.06″ (from about 3 to 1000 s⁻¹) and L/D ratio of 20 and diameter of 0.012″ (from about 1000 to 100000 s¹) respectively.

In an embodiment of the invention, the polyethylene composition or a molded article made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 100% of at least about 3 hrs., as measured according to ASTM D1693 (at 50° C. using 100% Igepal, condition B).

In an embodiment of the invention, the polyethylene composition or a molded article made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 100% of at least about 3.5 hrs, as measured according to ASTM D1693 (at 50° C. using 100% Igepal, condition B).

In an embodiment of the invention, the polyethylene composition or a molded article made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 100% of at least about 4.0 hrs., as measured according to ASTM D1693 (at 50° C. using 100% Igepal, condition B).

In an embodiment of the invention, the polyethylene composition or a molded article made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 100% of from about 3.5 to about 15 hrs., as measured according to ASTM D1693 (at 50° C. using 100% Igepal, condition B).

In an embodiment of the invention, the polyethylene composition or a molded article made from the polyethylene composition, has an environment stress crack resistance ESCR Condition B at 100% of from about 3.5 to about 12 hrs., as measured according to ASTM D1693 (at 50° C. using 100% Igepal, condition B).

In an embodiment of the invention, the polyethylene composition or a molded article made from the polyethylene composition has a notched Izod impact strength of at least about 40 J/m, as measured according to ASTM D256.

In embodiments of the invention, the polyethylene composition has a TD/MD shrinkage ratio (for an injection molded disk at about 48 hrs post molding) of from about 0.90 to about 1.20, or from about 0.90 to about 1.15, or from about 0.95 to about 1.15, or from about 0.90 to about 1.10, or from about 0.95 to about 1.10, or from about 0.95 to about 1.05 when measured according to the Dimensional Stability Test (DST).

In embodiments of the invention, the polyethylene composition has a TD shrinkage—MD shrinkage (for an injection molded disk at about 48 hour post molding time) of from about 0.25 to about 0.25, or from about 0.20 to about 0.20, or from about 0.15 to about 0.15, or from about 0.10 to about 0.10, or from about 0.075 to about 0.075, or from about 0.05 to about 0.05, when measured according to the Dimensional Stability Test (DST).

In an embodiment of the invention the polyethylene composition of the current invention has a density of from 0.950 to 0.960 g/cm³; a melt index I₂, of from 3 to 12 g/10 min; a molecular weight distribution M_(w)/M_(n), of from 2.0 to 7.0; a number average molecular weight M_(n), of below 30,000; a shear viscosity at 10⁵ s⁻¹ (240° C.) of less than 10 (Pa·s), a hexane extractables of less than 0.55%, a notched Izod impact strength of more than 40 J/m, and an ESCR B at 100% of at least about 3.5 hrs.

In an embodiment of the invention, the polyethylene composition has a hexanes extractables of less than about 0.55%. In further embodiments of the invention, the polyethylene composition has a hexanes extractables of less than about 0.50%, or less than about 0.45%, or less than about 0.40%, or less than about 0.35%.

In an embodiment of the invention, the polyethylene composition has a stress exponent, defined as Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16], which is ≦1.40. In further embodiments of the invention, the polyethylene composition has a stress exponent, Log₁₀[I₆/I₂]/Log₁₀[6.48/2.16] of from 1.22 to 1.40, or from 1.22 to 1.38, or from 1.24 to 1.36.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI(50)), as determined by temperature elution fractionation (TREF), of ≧about 60 weight percent. In further embodiments of the invention, the polyethylene composition will have a CDBI(50) of greater than about 65%, or greater than about 70%, or greater than about 75%, or greater than about 80%.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI(25)), as determined by temperature elution fractionation (TREF), of ≧about 55 weight percent. In further embodiments of the invention, the polyethylene composition will have a CDBI(25) of greater than about 60%, or greater than about 65%, or from about 55 to about 75%, or from about 60 to about 75%.

The polyethylene composition of this invention can be made using any conventional blending method such as but not limited to physical blending and in-situ blending by polymerization in multi reactor systems. For example, it is possible to perform the mixing of the first ethylene copolymer with the second ethylene copolymer by molten mixing of the two preformed polymers. One embodiment uses processes in which the first and second ethylene copolymers are prepared in at least two sequential polymerization stages, however, both in-series or an in-parallel dual reactor process are contemplated for use in the current invention. Gas phase, slurry phase or solution phase reactor systems may be used. In one embodiment a solution phase reactor systems is used.

Mixed catalyst single reactor systems may also be employed to make the polymer compositions of the present invention.

In an embodiment of the current invention, a dual reactor solution polymerization process is used as has been described in for example U.S. Pat. No. 6,372,864 and U.S. Pat. Appl. No. 20060247373A1 which are incorporated herein by reference.

Generally, the catalysts used in the current invention will be so called single site catalysts based on a group 4 metal having at least one cyclopentadienyl ligand. Examples of such catalysts include metallocenes, constrained geometry catalysts and phosphinimine catalysts used, for example, in combination with activators selected from methylaluminoxanes, boranes or ionic borate salts and are further described in U.S. Pat. Nos. 3,645,992; 5,324,800; 5,064,802; 5,055,438; 6,689,847; 6,114,481 and 6,063,879. Such single site catalysts are distinguished from traditional Ziegler-Natta or Phillips catalysts which are also well known in the art. In general, single site catalysts produce ethylene copolymers having a molecular weight distribution (M_(w)/M_(n)) of less than about 3.0 and a composition distribution breadth index CDBI(50) of greater than about 65%.

In an embodiment of the invention, a single site catalyst is used to make an ethylene copolymer having a CDBI(50) of at least about 65% by weight, or at least about 70%, or at least about 75%, or at least about 80%, or at least about 85%, during solution phase polymerization in a single reactor, for the preparation of each of the first and the second ethylene copolymers.

In an embodiment of the invention, homogeneously branched ethylene copolymers are prepared using an organometallic complex of a group 3, 4 or 5 metal that is further characterized as having a phosphinimine ligand. Such a complex, when active toward olefin polymerization, is known generally as a phosphinimine (polymerization) catalyst. Some non-limiting examples of phosphinimine catalysts can be found in U.S. Pat. Nos. 6,342,463; 6,235,672; 6,372,864; 6,984,695; 6,063,879; 6,777,509 and 6,277,931 all of which are incorporated by reference herein.

Some non-limiting examples of metallocene catalysts can be found in U.S. Pat. Nos. 4,808,561; 4,701,432; 4,937,301; 5,324,800; 5,633,394; 4,935,397; 6,002,033 and 6,489,413, which are incorporated herein by reference. Some non-limiting examples of constrained geometry catalysts can be found in U.S. Pat. Nos. 5,057,475; 5,096,867; 5,064,802; 5,132,380; 5,703,187 and 6,034,021, all of which are incorporated by reference herein in their entirety.

In an embodiment of the invention, use of a single site catalyst that does not produce long chain branching (LCB) is used. Hexyl (C6) branches detected by NMR are excluded from the definition of a long chain branch in the present invention.

Without wishing to be bound by any single theory, long chain branching can increase viscosity at low shear rates, thereby negatively impacting cycle times during the manufacture of caps and closures, such as during the process of compression molding. Long chain branching may be determined using ¹³C NMR methods and may be quantitatively assessed using the method disclosed by Randall in Rev. Macromol. Chem. Phys. C29 (2 and 3), p. 285.

In an embodiment of the invention, the polyethylene composition will contain fewer than 0.3 long chain branches per 1000 carbon atoms. In another embodiment of the invention, the polyethylene composition will contain fewer than 0.01 long chain branches per 1000 carbon atoms.

In an embodiment of the invention, the polyethylene composition is prepared by contacting ethylene and at least one alpha-olefin with a polymerization catalyst under solution phase polymerization conditions in at least two polymerization reactors (for an example of solution phase polymerization conditions see for example U.S. Pat. Nos. 6,372,864 and 6,984,695 and U.S. Patent Application 20060247373A1 which are incorporated herein by reference).

In an embodiment of the invention, the polyethylene composition is prepared by contacting at least one single site polymerization catalyst system (comprising at least one single site catalyst and at least one activator) with ethylene and a least one comonomer (e.g., a C3-C8 alpha-olefin) under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the invention, a group 4 single site catalyst system, comprising a single site catalyst and an activator, is used in a solution phase dual reactor system to prepare a polyethylene composition by polymerization of ethylene in the presence of an alpha-olefin comonomer.

In an embodiment of the invention, a group 4 single site catalyst system, comprising a single site catalyst and an activator, is used in a solution phase dual reactor system to prepare a polyethylene composition by polymerization of ethylene in the presence of 1-octene.

In an embodiment of the invention, a group 4 phosphinimine catalyst system, comprising a phosphinimine catalyst and an activator, is used in a solution phase dual reactor system to prepare a polyethylene composition by polymerization of ethylene in the presence of an alpha-olefin comonomer.

In an embodiment of the invention, a group 4 phosphinimine catalyst system, comprising a phosphinimine catalyst and an activator, is used in a solution phase dual reactor system to prepare a polyethylene composition by polymerization of ethylene in the presence of 1-octene.

In an embodiment of the invention, a solution phase dual reactor system comprises two solution phase reactors connected in series.

In an embodiment of the invention, a polymerization process to prepare the polyethylene composition comprises contacting at least one single site polymerization catalyst system (comprising at least one single site catalyst and at least one activator) with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in at least two polymerization reactors.

In an embodiment of the invention, a polymerization process to prepare the polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in a first reactor and a second reactor configured in series.

In an embodiment of the invention, a polymerization process to prepare the polyethylene composition comprises contacting at least one single site polymerization catalyst system with ethylene and at least one alpha-olefin comonomer under solution polymerization conditions in a first reactor and a second reactor configured in series, with the at least one alpha-olefin comonomer being fed exclusively to the first reactor.

In one embodiment, the production of the polyethylene composition of the present invention may include an extrusion or compounding step. Such steps are well known in the art.

In one embodiment, the polyethylene composition can comprise further polymer components in addition to the first and second ethylene polymers. Such polymer components include polymers made in situ or polymers added to the polymer composition during an extrusion or compounding step.

Optionally, additives can be added to the polyethylene composition. Additives can be added to the polyethylene composition during an extrusion or compounding step, but other suitable known methods will be apparent to a person skilled in the art. The additives can be added as is or as part of a separate polymer component (i.e. not the first or second ethylene polymers described above) added during an extrusion or compounding step. Suitable additives are known in the art and include but are not-limited to antioxidants, phosphites and phosphonites, nitrones, antacids, UV light stabilizers, UV absorbers, metal deactivators, dyes, fillers and reinforcing agents, nano-scale organic or inorganic materials, antistatic agents, lubricating agents such as calcium stearates, slip additives such as erucimide, and nucleating agents (including nucleators, pigments or any other chemicals which may provide a nucleating effect to the polyethylene composition). The additives that can be optionally added may be added in amount of up to about 20 weight percent (wt %).

One or more nucleating agent(s) may be introduced into the polyethylene composition by kneading a mixture of the polymer, usually in powder or pellet form, with the nucleating agent, which may be utilized alone or in the form of a concentrate containing further additives such as stabilizers, pigments, antistatics, UV stabilizers and fillers. It should be a material which is wetted or absorbed by the polymer, which is insoluble in the polymer and of melting point higher than that of the polymer, and it should be homogeneously dispersible in the polymer melt in as fine a form as possible (about 1 to about 10 μm). Compounds known to have a nucleating capacity for polyolefins include salts of aliphatic monobasic or dibasic acids or arylalkyl acids, such as sodium succinate or aluminum phenylacetate; and alkali metal or aluminum salts of aromatic or alicyclic carboxylic acids such as sodium β-naphthoate. Another compound known to have nucleating capacity is sodium benzoate. The effectiveness of nucleation may be monitored microscopically by observation of the degree of reduction in size of the spherulites into which the crystallites are aggregated.

In an embodiment of the invention, the polyethylene compositions described above are used in the formation of molded articles. For example, articles formed by compression molding and injection molding are contemplated. Such articles include, for example, caps, screw caps, and closures for bottles, containers and the like. However, a person skilled in the art will readily appreciate that the compositions described above may also be used for other applications such as but not limited to film, injection blow molding, blow molding and sheet extrusion applications.

In an embodiment of the invention, the polyethylene compositions described above are used in the formation of a closure for bottles, containers and the like. For example, closures for bottles formed by compression molding or injection molding are contemplated. Such closures include, for example, hinged caps, hinged screw caps, hinged snap-top caps, and hinged closures for bottles, containers and the like.

In an embodiment of the invention, a closure (or cap) is a screw cap for a bottle, container and the like.

In an embodiment of the invention, a closure (or cap) comprises a hinge made of the same material as the rest of the closure (or cap).

In an embodiment of the invention, a closure (or cap) is hinged closure.

In an embodiment of the invention, a closure (or cap) is a hinged closure for bottles, containers and the like.

In an embodiment of the invention, a closure (or cap) is a flip-top hinge closure, such as a flip-top hinge closure for use on a plastic ketchup bottle or similar containers containing foodstuffs.

When a closure is a hinged closure, it comprises a hinged component and generally consists of at least two bodies which are connected by a thinner section that acts as a hinge allowing the at least two bodies to bend from an initially molded position. The thinner section may be continuous or web-like, wide or narrow.

A useful closure (for bottles, containers and the like) is a hinged closure and may consist of two bodies joined to each other by at least one thinner bendable portion (e.g. the two bodies can be joined by a single bridging portion, or more than one bridging portion, or by a webbed portion, etc.). A first body may contain a dispensing hole and which may snap onto or screw onto a container to cover a container opening (e.g. a bottle opening) while a second body may serve as a snap on lid which may mate with the first body.

The caps and closures, of which hinged caps and closures are a subset, can be made according to any known method, including for example injection molding and compression molding techniques that are well known to persons skilled in the art. Hence, in an embodiment of the invention a closure (or cap) comprising the polyethylene composition (defined above) is prepared with a process comprising at least one compression molding step and/or at least one injection molding step.

In one embodiment, the caps and closures (including single piece or multi-piece variants including hinged variants) comprise the polyethylene composition described above and have very good dimensional stability, good organoleptic properties, good toughness, as well as reasonable ESCR values. Hence the closures and caps of this embodiment are well suited for sealing bottles, containers and the like, for examples bottles that may contain drinkable water, and other foodstuffs, including but not limited to liquids that are non-pressurized. The closures and caps may also be used for sealing bottles containing drinkable water or non-carbonated beverages (e.g. juice). Other applications, include caps and closures for bottles and containers containing foodstuffs, such as for example ketchup bottles and the like.

In an embodiment of the invention, homogeneously branched ethylene copolymers are prepared using an organometallic complex of a group 3, 4 or 5 metal that is further characterized as having a phosphinimine ligand. Such a complex, when active toward olefin polymerization, is known generally as a phosphinimine (polymerization) catalyst.

An embodiment of the invention is a closure, for example a closure for a bottle, a container and the like, the closure being a hinged closure comprising a polyethylene composition, the polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³;

wherein the density of the second ethylene copolymer is less than

0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs.

In an embodiment of the invention, the polyethylene composition has a TD/MD shrinkage ratio of from about 0.90 to about 1.15 when measured according to the Dimensional Stability Test (DST).

In an embodiment of the invention, the polyethylene composition has an ESCR Condition B (100% IGEPAL) of from about 3.5 to about 15 hrs.

In an embodiment of the invention, the polyethylene composition has a melt index I₂, of greater than 5.0 to less than 20 g/10 min.

In an embodiment of the invention, the first and second ethylene copolymers are made by polymerizing ethylene and an alpha olefin in the presence of a single site catalyst.

In an embodiment of the invention, the density of the second ethylene copolymer is less than 0.030 g/cm³ higher than the density of the first ethylene copolymer.

In an embodiment of the invention, the first ethylene copolymer has a melt index I₂, of from 0.1 to 3.0 g/10 min.

In an embodiment of the invention, the second ethylene copolymer has a melt index I₂, of from 100 to 5000 g/10 min.

In an embodiment of the invention, the polyethylene composition has a melt index I₂, of from 6 to 12 g/10 min.

In an embodiment of the invention, the polyethylene composition has a bimodal molecular weight distribution as determined by gel permeation chromatography.

In an embodiment of the invention, the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is at least 1.5.

In an embodiment of the invention, the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.5 to 6.

In an embodiment of the invention, the first ethylene copolymer has a density of from 0.936 to 0.952 g/cm³.

In an embodiment of the invention, the second ethylene copolymer has a density of less than 0.965 g/cm³.

In an embodiment of the invention, the polyethylene composition has a density of from 0.952 to 0.960 g/cm³.

In an embodiment of the invention, the polyethylene composition has no long chain branching.

In an embodiment of the invention, the first and second ethylene copolymers have a M_(w)/M_(n) of less than 2.5.

In an embodiment of the invention, the polyethylene composition has a composition distribution breadth index (CDBI(50)) of greater than about 65 wt %.

In an embodiment of the invention, the first and second ethylene copolymers each have a composition distribution breadth index (CDBI(50)) of greater than about 65 wt %.

In an embodiment of the invention, the polyethylene composition comprises: from about 25 to about 60 wt % of the first ethylene copolymer; and from about 75 to about 40 wt % of the second ethylene copolymer.

In an embodiment of the invention, the polyethylene composition has a comonomer content of less than about 0.5 mol % as determined by ¹³C NMR.

In an embodiment of the invention, the polyethylene composition further comprises a nucleating agent or a combination of nucleating agents.

In an embodiment of the invention, the first and second ethylene copolymers are copolymers of ethylene and 1-octene.

In an embodiment of the invention, the closure is made by compression molding or injection molding.

In an embodiment of the invention, the closure is a screw cap.

In an embodiment of the invention, the polyethylene composition is prepared by contacting ethylene and an alpha-olefin with a single site polymerization catalyst under solution polymerization conditions in a least two polymerization reactors.

An embodiment of the invention is a closure, for example a closure for a bottle, a container and the like, the closure being a hinged closure comprising a polyethylene composition.

An embodiment of the invention is a process for preparing a closure, for example a closure for a bottle, a container and the like, the closure being a hinged closure, wherein the process comprises at least one compression molding or injection molding step and wherein the closure comprises a polyethylene composition, the polyethylene composition comprising:

(1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and

(2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³;

wherein the density of the second ethylene copolymer is less than

0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs.

The invention is further illustrated by the following non-limiting examples. Unless otherwise indicated, all percentages are by weight unless otherwise specified.

EXAMPLES

Melt indexes, I₂, I₅, I₆ and I₂₁ for the polyethylene composition were measured according to ASTM D1238 (when conducted at 190° C., using a 2.16 kg, a 5 kg, a 6.48 kg and a 21 kg weight respectively).

M_(n), M_(w), and M_(z) (g/mol) were determined by high temperature Gel Permeation Chromatography with differential refractive index detection using universal calibration (e.g. ASTM-D6474-99). GPC data was obtained using an instrument sold under the trade name “Waters 150c”, with 1,2,4-trichlorobenzene as the mobile phase at 140° C. The samples were prepared by dissolving the polymer in this solvent and were run without filtration. Molecular weights are expressed as polyethylene equivalents with a relative standard deviation of 2.9% for the number average molecular weight (“Mn”) and 5.0% for the weight average molecular weight (“Mw”). The molecular weight distribution (MWD) is the weight average molecular weight divided by the number average molecular weight, M_(w)/M_(n). The z-average molecular weight distribution is M_(z)/M_(n). Polymer sample solutions (1 to 2 mg/mL) were prepared by heating the polymer in 1,2,4-trichlorobenzene (TCB) and rotating on a wheel for 4 hours at 150° C. in an oven. The antioxidant 2,6-di-tert-butyl-4-methylphenol (BHT) was added to the mixture in order to stabilize the polymer against oxidative degradation. The BHT concentration was 250 ppm. Sample solutions were chromatographed at 140° C. on a PL 220 high-temperature chromatography unit equipped with four Shodex columns (HT803, HT804, HT805 and HT806) using TCB as the mobile phase with a flow rate of 1.0 mL/minute, with a differential refractive index (DRI) as the concentration detector. BHT was added to the mobile phase at a concentration of 250 ppm to protect the columns from oxidative degradation. The sample injection volume was 200 mL. The raw data were processed with Cirrus GPC software. The columns were calibrated with narrow distribution polystyrene standards. The polystyrene molecular weights were converted to polyethylene molecular weights using the Mark-Houwink equation, as described in the ASTM standard test method D6474.

Primary melting peak (° C.), heat of fusion (J/g) and crystallinity (%) was determined using differential scanning calorimetry (DSC) as follows: the instrument was first calibrated with indium; after the calibration, a polymer specimen is equilibrated at 0° C. and then the temperature was increased to 200° C. at a heating rate of 10° C./min; the melt was then kept isothermally at 200° C. for five minutes; the melt was then cooled to 0° C. at a cooling rate of 10° C./min and kept at 0° C. for five minutes; the specimen was then heated to 200° C. at a heating rate of 10° C./min. The DSC Tm, heat of fusion and crystallinity are reported from the 2^(nd) heating cycle.

The short chain branch frequency (SCB per 1000 carbon atoms) of the polyethylene composition was determined by Fourier Transform Infrared Spectroscopy (FTIR) as per the ASTM D6645-01 method. A Thermo-Nicolet 750 Magna-IR Spectrophotometer equipped with OMNIC version 7.2a software was used for the measurements. Unsaturations in the polyethylene composition were also determined by Fourier Transform Infrared Spectroscopy (FTIR) as per ASTM D3124-98. Comonomer content can also be measured using ¹³C NMR techniques as discussed in Randall, Rev. Macromol. Chem. Phys., C29 (2&3), p 285; U.S. Pat. No. 5,292,845 and WO 2005/121239.

Polyethylene composition density (g/cm³) was measured according to ASTM D792.

Hexane extractables were determined according to ASTM D5227.

Shear viscosity was measured by using a Kayeness WinKARS Capillary Rheometer (model #D5052M-115). For the shear viscosity at lower shear rates, a die having a die diameter of 0.06 inch and L/D ratio of 20 and an entrance angle of 180 degrees was used. For the shear viscosity at higher shear rates, a die having a die diameter of 0.012 inch and L/D ratio of 20 was used.

The Processability Indicator:

The “processability indicator” as used herein is defined as:

Processability Indicator=100/η(10⁵ s⁻¹, 240° C.);

where η is the shear viscosity measured at 10⁵ 1/s at 240° C.

To determine CDBI(50), a solubility distribution curve is first generated for the polyethylene composition. This is accomplished using data acquired from the TREF technique. This solubility distribution curve is a plot of the weight fraction of the copolymer that is solubilized as a function of temperature. This is converted to a cumulative distribution curve of weight fraction versus comonomer content, from which the CDBI(50) is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 50% of the median comonomer content on each side of the median (See WO 93/03093 and U.S. Pat. No. 5,376,439). The CDBI(25) is determined by establishing the weight percentage of a copolymer sample that has a comonomer content within 25% of the median comonomer content on each side of the median

The temperature rising elution fractionation (TREF) method used herein was as follows. Polymer samples (50 to 150 mg) were introduced into the reactor vessel of a crystallization-TREF unit (Polymer ChAR™). The reactor vessel was filled with 20 to 40 ml 1,2,4-trichlorobenzene (TCB), and heated to the desired dissolution temperature (e.g., 150° C.) for 1 to 3 hours. The solution (0.5 to 1.5 ml) was then loaded into the TREF column filled with stainless steel beads. After equilibration at a given stabilization temperature (e.g., 110° C.) for 30 to 45 minutes, the polymer solution was allowed to crystallize with a temperature drop from the stabilization temperature to 30° C. (0.1 or 0.2° C./minute). After equilibrating at 30° C. for 30 minutes, the crystallized sample was eluted with TCB (0.5 or 0.75 mL/minute) with a temperature ramp from 30° C. to the stabilization temperature (0.25 or 1.0° C./minute). The TREF column was cleaned at the end of the run for 30 minutes at the dissolution temperature. The data were processed using Polymer ChAR software, Excel spreadsheet and TREF software developed in-house.

High temperature GPC equipped with an online FTIR detector (GPC-FTIR) was used to measure the comonomer content as the function of molecular weight.

Plaques molded from the polyethylene compositions were tested according to the following ASTM methods: Bent Strip Environmental Stress Crack Resistance (ESCR) at Condition B at 100% IGEPAL at 50° C., ASTM D1693; notched Izod impact properties, ASTM D256; Flexural Properties, ASTM D 790; Tensile properties, ASTM D 638; Vicat softening point, ASTM D 1525; Heat deflection temperature, ASTM D 648.

Dynamic mechanical analyses were carried out with a rheometer, namely Rheometrics Dynamic Spectrometer (RDS-II) or Rheometrics SR5 or ATS Stresstech, on compression molded samples under nitrogen atmosphere at 190° C., using 25 mm diameter cone and plate geometry. The oscillatory shear experiments were done within the linear viscoelastic range of strain (10% strain) at frequencies from 0.05 to 100 rad/s. The values of storage modulus (G′), loss modulus (G″), complex modulus (G*) and complex viscosity (η*) were obtained as a function of frequency. The same rheological data can also be obtained by using a 25 mm diameter parallel plate geometry at 190° C. under nitrogen atmosphere.

Dimensional Stability Test (DST):

The dimensional stability of the polyethylene compositions was determined as follows: A 150-ton×12-Oz Cincinnati Milacron injection molding machine (Hydradamp 150 T 12 oz PC-111, serial #4001 A21/79-38) with a 2 inch (50.8 mm) screw was used to produce parts according to the conditions listed in Table 1. The mold was an ASTM test mold, which makes tensile test specimens with an overall length of 1.30 inches, an overall width of 0.75 inch, and a thickness of 0.12 inch; tensile test specimens with an overall length of 1.375 inch, an overall width of 0.375 inch, and a thickness of 0.12 inch; tensile test specimens with an overall length of 2.5 inch, an overall width of 0.375 inch, and a thickness of 0.12 inch; flexural modulus bars with a length of 5 inch, a width of 0.50 inch, and a thickness of either 0.12 inch or 0.75 inch, and an impact round disk with a diameter of 2 inch and a thickness of 0.12 inch. Immediately after molding, the injection-molded disk was removed from the runner (note: an injection molded disk with a 2 inch diameter and a thickness of 0.12 inches was used for measurements in the present invention). The diameters in both the machine (or in-flow) direction (MD) and transverse-flow direction (TD) are then measured at room temperature (23±2° C.) after 1, 24 and 48 hrs. of molding. Shrinkage at time t is defined as the percentage change in dimension at measurement time from the original mold dimensions:

Shrinkage percent=(Mold dimension−Specimen dimension at time t)×100/Mold dimension

Thus, MD shrinkage is the shrinkage measured on the disk in the flow direction, and Transverse direction (TD) shrinkage is the shrinkage measured in the cross-flow direction. Here, the isotropic shrinkage is defined as the equal shrinkage in both the flow direction (in-flow) and the transverse direction. Differential shrinkage is defined as TD shrinkage minus MD shrinkage (an indication of part planarity or flatness or the extent of part warpage). The smaller the difference it is, the better the part planarity. A TD/MD shrinkage ratio, the TD shrinkage divided by MD shrinkage, can also be used as a measure of the extent of isotropic shrinkage (the closer to unity it is, the better the part planarity). The molding parameters used are summarized in Table 1.

TABLE 1 Barrel Temperature (° C.), feed Section 215.5 Barrel Temperature (° C.), Trans. Section 237.8 Barrel Temperature (° C.), Metering Section 237.8 Barrel Temperature (° C.), Nozzle 237.8 Injection Time - High (s) 6 Injection Time - Low (s) 23 Cooling Time (s) 30 Decompression Time (s) 0.07 Clamp Open Time (s) 0.02 Mold Close Time (s) 60 Cycle Time (s) 62 Screw Speed (rpm) 20 Injection rate Max Shot size (inch) 1.5 Cushion (inch) 0.2 Injection Pressure - High (psi) 5250 Injection Pressure - Low (psi) 5000 Back Pressure (psi) 1000 Clamp Pressure - High (psi) 1850 Clamp Pressure - Low (psi) 1000 Mold Temperature (° C.), represented by cooling 11.7 water Cycle Auto

Examples of the polyethylene compositions were produced in a dual reactor solution polymerization process in which the contents of the first reactor flow into the second reactor. This in-series “dual reactor” process produces an “in-situ” polyethylene blend (i.e., the polyethylene composition). Note, that when an in-series reactor configuration is used, un-reacted ethylene monomer, and un-reacted alpha-olefin comonomer present in the first reactor will flow into the downstream second reactor for further polymerization.

In the present inventive examples, although no co-monomer is feed directly to the downstream second reactor, an ethylene copolymer is nevertheless formed in second reactor due to the significant presence of un-reacted 1-octene flowing from the first reactor to the second reactor where it is copolymerized with ethylene. Each reactor is sufficiently agitated to give conditions in which components are well mixed. The volume of the first reactor was 12 liters and the volume of the second reactor was 22 liters. These are the pilot plant scales. The first reactor was operated at a pressure of 10500 to 35000 kPa and the second reactor was operated at a lower pressure to facilitate continuous flow from the first reactor to the second. The solvent employed was methylpentane. The process operates using continuous feed streams. The catalyst employed in the dual reactor solution process experiments was a phosphinimine catalyst, which was a titanium complex having a phosphinimine ligand (e.g., (tert-butyl)₃P=N), a cyclopentadienide ligand (e.g., Cp) and two activatable ligands, such as but not limited to chloride ligands (note: “activatable ligands” are removed, by for example electrophilic abstraction using a co-catalyst or activator to generate an active metal center). A boron based co-catalyst (e.g., Ph₃CB(C₆F₅)₄) was used in approximately stoichiometric amounts relative to the titanium complex. Commercially available methylaluminoxane (MAO) was included as a scavenger at an Al:Ti of about 40:1. In addition, 2,6-di-tert-butylhydroxy-4-ethylbenzene was added to scavenge free trimethylaluminum within the MAO in a ratio of Al:OH of about 0.5:1.

Comparative polyethylene compositions (Comparative Examples 1-3) are made using a single site phosphinimine catalyst in a dual reactor solution process in which all the comonomer is fed to the second reactor.

Comparative polyethylene composition (Comparative Example 4) is an injection molding grade believed to be an ethylene homopolymer made with a traditional polymerization catalyst (e.g., a Ziegler-Natta polymerization catalyst) and which is commercially available from Ineos as J60-800-178.

Comparative polyethylene composition (Comparative Example 5) is an injection molding grade polyethylene homopolymer, commercially available resin from NOVA Chemicals as IG-454-A.

Comparative polyethylene compositions (Comparative Examples 6, 7 and 8) are made using a single site phosphinimine catalyst in a dual reactor solution process according to U.S. Pat. No. 8,022,143 and CA Application 2,752,407. Comparative resin 6 has a density of 0.952 g/cm³, a high load melt index I₂₁ of 71 g/10 min and a melt index ratio I₂₁/I₂ of 48.5. Comparative resin 7 has a density of 0.952 g/cm³ a high load melt index I₂₁ of 71 g/10 min and a melt index ratio I₂₁/I₂ of 55. Comparative resin 8 has a density of 0.953 g/cm³, a high load melt index I₂₁ of 80.2 g/10 min and a melt index ratio I₂₁/I₂ of 64.4.

Inventive polyethylene compositions (Inventive Examples 1-6) are made using a single site phosphinimine catalyst in a dual reactor solution process as described above and have an ESCR at condition B100 of greater than 3.5 hours and a SCB1/SCB2 ratio of greater than 1.0. These inventive examples also have a Mz value of less than 300,000.

The polymerization conditions used to make the inventive compositions are provided in Table 2.

Inventive and comparative polyethylene composition properties are described in Tables 3.

Calculated properties for the first ethylene copolymer and the second ethylene copolymer for selected comparative and inventive polyethylene compositions are provided in Table 4 (see “Copolymerization Reactor Modeling” below for methods).

The properties of pressed plaques made from comparative and inventive polyethylene compositions are provided in Table 5.

Information on dimensional stability for inventive and comparative resins is provided in Table 6.

Copolymerization Reactor Modeling

For multicomponent (or bimodal resins) polyethylene polymers with very low comonomer content, it can be difficult to reliably estimate the short chain branching (and subsequently polyethylene resin density by combining other information) of each polymer component by mathematical deconvolution of GPC-FTIR data, as was done in, for example, U.S. Pat. No. 8,022,143. Instead, the M_(w), M_(n), M_(z), M_(w)/M_(n) and the short chain branching per thousand carbons (SCB/1000C) of the first and second copolymers were calculated herein, by using a reactor model simulation using the input conditions which were employed for actual pilot scale run conditions (for references on relevant reactor modeling methods, see “Copolymerization” by A. Hamielec, J. MacGregor, and A. Penlidis in Comprehensive Polymer Science and Supplements, volume 3, Chapter 2, page 17, Elsevier, 1996 and “Copolymerization of Olefins in a Series of Continuous Stirred-Tank Slurry-Reactors using Heterogeneous Ziegler-Natta and Metallocene Catalysts. I. General Dynamic Mathemacial Model” by J. B. P Soares and A. E Hamielec in Polymer Reaction Engineering, 4(2&3), p 153, 1996.) This type of model is considered reliable for the estimate of comonomer (e.g., 1-octene) content even at low comonomer incorporation levels, since the ethylene conversion, ethylene input flow and comonomer input flow can be obtained directly from the experimental conditions and because the reactive ratio (see below) can be reliably estimated for the catalyst system used in the present invention. For clarity, the “monomer” or “monomer 1” represent ethylene, while the terms “comonomer” or “monomer 2”, represent 1-octene.

The model takes for input the flow of several reactive species (e.g. catalyst, monomer such as ethylene, comonomer such as 1-octene, hydrogen, and solvent) going to each reactor, the temperature (in each reactor), and the conversion of monomer (in each reactor), and calculates the polymer properties (of the polymer made in each reactor, i.e., the first and second ethylene copolymers) using a terminal kinetic model for continuously stirred tank reactors (CSTRs) connected in series. The “terminal kinetic model” assumes that the kinetics depend upon the monomer unit within the polymer chain on which the active catalyst site is located (see “Copolymerization” by A. Hamielec, J. MacGregor, and A. Penlidis in Comprehensive Polymer Science and Supplements, Volume 3, Chapter 2, page 17, Elsevier, 1996). In the model, the copolymer chains are assumed to be of reasonably large molecular weight to ensure that the statistics of monomer/comonomer unit insertion at the active catalyst center is valid and that monomers/comonomers consumed in routes other than propagation are negligible. This is known as the “long chain” approximation.

The terminal kinetic model for polymerization includes reaction rate equations for activation, initiation, propagation, chain transfer, and deactivation pathways. This model solves the steady-state conservation equations (e.g., the total mass balance and heat balance) for the reactive fluid which comprises the reactive species identified above.

The total mass balance for a generic CSTR with a given number of inlets and outlets is given by:

0=Σ_(i){dot over (m)}_(i)   (1)

where {dot over (m)}_(i) represents the mass flow rate of individual streams with index i indicating the inlet and outlet streams.

Equation (1) can be further expanded to show the individual species and reactions:

$\begin{matrix} {0 = {\frac{\Sigma_{i}\frac{m{\overset{.}{x}}_{ij}}{M_{i}}}{\rho_{mix}V} + {R_{j}/\rho_{mix}}}} & (2) \end{matrix}$

where M_(i) is the average molar weight of the fluid inlet or outlet (i), x_(ij) is the mass fraction of species j in stream i, ρ_(mix) is the molar density of the reactor mixture, V is the reactor volume, R_(j) is the reaction rate for species j, which has units of kmol/m³s.

The total heat balance is solved for an adiabatic reactor and is given by:

0=(Σ{dot over (m)} _(i) ΔH _(i) +q _(Rx) V+{dot over (W)}−{dot over (Q)})   (2)

where, {dot over (m)}_(i) is the mass flow rate of stream i (inlet or outlet), ΔH_(i) is the difference in enthalpy of stream i versus a reference state , q_(Rx) is the heat released by reaction(s), V is the reactor volume, {dot over (W)} is the work input (i.e., agitator), {dot over (Q)} is the heat input/loss.

The catalyst concentration input to each reactor is adjusted to match the experimentally determined ethylene conversion and reactor temperature values in order solve the equations of the kinetic model (e.g., propagation rates, heat balance and mass balance).

The H₂ concentration input to each reactor may be likewise adjusted so that the calculated molecular weight distribution of a polymer made over both reactors (and, hence, the molecular weight of polymer made in each reactor) matches that which is observed experimentally.

The degree of polymerization (DPN) for a polymerization reaction is given by the ratio of the rate of chain propagation reactions over the rate of chain transfer/termination reactions:

$\begin{matrix} {{DPN} = \frac{{k_{p\; 11}{\varphi_{1}\left\lbrack m_{1} \right\rbrack}} + {k_{p\; 12}{\varphi_{1}\left\lbrack m_{2} \right\rbrack}} + {k_{p\; 21}{\varphi_{2}\left\lbrack m_{2} \right\rbrack}}}{{{k_{{tm}\; 11}\left\lbrack m_{1} \right\rbrack}\varphi_{1}} + {{k_{{tm}\; 12}\left\lbrack m_{2} \right\rbrack}\varphi_{1}} + {{k_{{tm}\; 21}\left\lbrack m_{2} \right\rbrack}\varphi_{2}} + {k_{{ts}\; 1}\varphi_{1}} + {k_{{ts}\; 2}\varphi_{2}} + {k_{{tH}\; 1}\lbrack H\rbrack} + {k_{{tH}\; 2}\lbrack H\rbrack}}} & (4) \end{matrix}$

where k_(p12) is the propagation rate constant for adding monomer 2 to a growing polymer chain ending with monomer 1, [m₁] is the molar concentration of monomer 1 (ethylene) in the reactor, [m₂] is the molar concentration of monomer 2 (1-octene) in the reactor, k_(tm12) the termination rate constant for chain transfer to monomer 2 for a growing chain ending with monomer 1, k_(ts1) is rate constant for the spontaneous chain termination for a chain ending with monomer 1, k_(tH1) is the rate constant for the chain termination by hydrogen for a chain ending with monomer 1. φ₁ and φ₂and the fraction of catalyst sites occupied by a chain ending with monomer 1 or monomer 2 respectively.

The number average molecular weight (Mn) for a polymer follows from the degree of polymerization and the molecular weight of a monomer unit. From the number average molecular weight of polymer in each reactor, and assuming a Flory distribution for a single site catalyst, the molecular weight distribution is determined for the polymer formed in each reactor:

w(n)=τ² ne ^(−τn)   (5)

where

${\tau = \frac{1}{DPN}},$

and w(n) is the weight fraction of polymer having a chain length n.

The Flory distribution can be transformed into the common log scaled GPC trace by applying:

$\begin{matrix} {\frac{W}{{\log (M)}} = {{\ln (10)}\frac{n^{2}}{{DPN}^{2}}^{({- \frac{n}{DPN}})}}} & (6) \end{matrix}$

where

$\frac{W}{{\log ({MW})}}$

is the differential weight fraction of polymer with a chain length n (n=MW/28 where 28 is the molecular weight of the polymer segment corresponding to a C₂H₄ unit) and DPN is the degree of polymerization as calculated by Equation (4). From the Flory model, the M_(w) and the M_(z) of the polymer made in each reactor are: M_(w)=2×M_(n) and M_(z)=1.5×M_(w).

The overall molecular weight distribution over both reactors is simply the sum of the molecular weight distribution of polymer made in each reactor, and where each Flory distribution is multiplied by the weight fraction of polymer made in each reactor:

$\begin{matrix} {\frac{\overset{\_}{W}}{{\log ({MW})}} = {{W_{R\; 1}\left( {{\ln (10)}\frac{n^{2}}{{DPN}_{R\; 1}^{2}}^{({- \frac{n}{{DPN}_{R\; 1}}})}} \right)} + {W_{R\; 2}\left( {{\ln (10)}\frac{n^{2}}{{DPN}_{R\; 2}^{2}}^{({- \frac{n}{{DPN}_{R\; 2}}})}} \right)}}} & (7) \end{matrix}$

where dW/dlog(MW) is the overall molecular weight distribution function, w_(R1) and W_(R2) are the weight fraction of polymer made in each reactor, DPN₁ and DPN₂ is the average chain length of the polymer made in each reactor (i.e. DPN₁=M_(nR1)/28). The weight fraction of material made in each reactor is determined from knowing the mass flow of monomer and comonomer into each reactor along with knowing the conversions for monomer and comonomer in each reactor.

The moments of the overall molecular weight distribution (or the molecular weight distribution of polymer made in each reactor) can be calculated using equations 8a, 8b and 8c (a Flory Model is assumed above, but the below generic formula apply to other model distributions as well):

$\begin{matrix} {\overset{\_}{M_{n}} = \frac{\Sigma_{i}w_{i}}{\Sigma_{i}\frac{w_{i}}{M_{i}}}} & \left( {8a} \right) \\ {\overset{\_}{M_{w}} = \frac{\Sigma_{i}w_{i}M_{i}}{\Sigma_{i}w_{i}}} & \left( {8b} \right) \\ {\overset{\_}{M_{z}} = \frac{\Sigma_{i}w_{i}M_{i}^{2}}{\Sigma_{i}w_{i}M_{i}}} & \left( {8c} \right) \end{matrix}$

The comonomer content in the polymer product (in each reactor) may also be calculated using the terminal kinetic model and long chain approximations discussed above (see A. Hamielec, J. MacGregor, and A. Penlidis. Comprehensive Polymer Science and Supplements, volume 3, chapter Copolymerization, page 17, Elsevier, 1996).

For a given catalyst system, the comonomer (e.g., 1-octene) incorporation is a function of the monomer (e.g., ethylene) conversion, the comonomer to monomer ratio in the reactor (γ) and the reactivity ratio of monomer 1 (e.g., ethylene) over monomer 2 (e.g., 1-octene):

r ₁ =k _(p11) /k _(p12).

For a CSTR, the molar ratio of ethylene to comonomer in the polymer (γ) can be estimated knowing the reactivity ratio r₁ of the catalsyt system and knowing the ethylene conversion in the reactor (Q_(m1)). A quadratic equation can be derived using the May and Lewis equation for instanstaneous comonomer incorporation (see “Copolymerization” by A. Hamielec, J. MacGregor, and A. Penlidis in Comprehensive Polymer Science and Supplements, Volume 3, Chapter 2, page 17, Elsevier, 1996) and solving the mass balance around the reaction. The molar ratio of ethylene to 1-octene in the polymer is the negative root of the following quadratic equation:

$\begin{matrix} {{{{- Y^{2}}\frac{\gamma}{4}} + {\left\lbrack {r_{1} + {Q_{m\; 1}\left( {1 - r_{1}} \right)} + \frac{\gamma}{4}} \right\rbrack Y} - Q_{m\; 1}} = 0} & (9) \end{matrix}$

where Y is the molar ratio of ethylene to 1-octene in the polymer, γ is the mass flow ratio of 1-octene to ethylene going the reactor, r₁ is the reactivity ratio of monomer 1 to monomer 2 for the catalyst system (r₁=k_(p11)/k_(p12)) and Q_(m1) is the ethylene monomer fractional conversion.

The branching frequency can then be calculated knowing the molar ratio of monomer 1 to monomer 2 in the polymer:

$\begin{matrix} {{BF} = \frac{500}{Y + 1}} & (10) \end{matrix}$

where Y, is the molar ratio of monomer 1 (ethylene) over monomer 2 (1-octene) in the polymer, and BF is the branching frequency (branches per 1000 carbon atoms).

The overall branching frequency distribution (BFD) of the ethylene composition can be calculated by knowing the molecular weight distribution and weight fraction of polymer made in each reactor, and the average branching frequency (BF) of the ethylene copolymer made in each reactor. The fraction of polymer made in each reactor can be calculated from the experimental mass flows and conversion of monomer and comonomer in each reactor. The branching frequency distribution function is obtained by calculating the average branch content for each molecular weight value of the overall molecular weight distribution function made from the two Flory distributions:

$\begin{matrix} {{BF}_{MW} = \frac{{w_{R\; 1}{BF}_{R\; 1}{F_{1}\left( {MW}_{R\; 1} \right)}} + {w_{R\; 2}{BF}_{R\; 2}{F_{2}\left( {MW}_{R\; 2} \right)}}}{{w_{R\; 1}{F_{1}\left( {MW}_{R\; 1} \right)}} + {w_{R\; 2}{F_{2}\left( {MW}_{R\; 2} \right)}}}} & (11) \end{matrix}$

where BF_(MW) is the branching at molecular weight (MW), w_(R1) and w_(R2) are the weight fraction of polymer made in Reactor 1 and Reactor 2, BF_(R1) and BF_(R2) are the average branching frequency of polymer made in R1 and R2 (from Equations 9 and 10), F₁(MW_(R1)) and F₂(MW_(R2)) are Flory distribution function from Reactor 1 and Reactor 2.

The overall branching frequency of the polyethylene composition is given by the weighted average of the branching frequency of the polymer made in each reactor:

BF _(avg) =w ₁ BF ₁ +w ₂ BF ₂   (12)

where, BF_(avg) is the average branching frequency for the total polymer (e.g. the polyethylene composition), w₁ and w₂ are the weight fraction of material made in each reactor, BF₁ and BF₂ are the branching frequency of material made in each reactor (e.g., the branching frequency of the first and second ethylene copolymers).

For the polymer obtained in each reactor, the key resin parameters which are obtained from the above described kinetic model are the molecular weights Mn, Mw and Mz, the molecular weight distributions M_(w)/M_(n) and Mz/Mw and the branching frequency (SCB/1000 Cs). With this information in hand, a component (or composition) density model and a component (or composition) melt index, I₂, model was used according to the following equations, which were empirically determined, to calculate the density and melt index I₂ of each of the first and second ethylene copolymers:

Density:

$\frac{1}{\rho} = {1.0142 + {0.0033\left( {1.22 \cdot {BF}} \right)^{0.8346}} + \frac{0.030\; k^{0.9804}}{1 + \frac{0.3712}{^{1.22\; {BF}}}}}$

where, BF is the branching frequency,

$k = {{Log}_{10}\left( \frac{M_{n}}{1000} \right)}$

Melt Index, I₂ (MI):

${{Log}_{10}({MI})} = {7.8998 - {3.9089\; {{Log}_{10}\left( \frac{M_{w}}{1000} \right)}} - {0.2799\frac{M_{n}}{M_{w}}}}$

Hence, the above models were used to estimate the branch frequency, weight fraction (or weight percent), melt index and the density of the polyethylene composition components, which were formed in each of reactor 1 and 2 (i.e. the first and second ethylene copolymers).

TABLE 2 Reactor Conditions for Inventive Examples Inventive Inventive Inventive Inventive Inventive Inventive Example No. Example #1 Example #2 Example #3 Example #4 Example #5 Example #6 Material Name PS 101801 PS 103550 PS 103562 PS 103574 PS 103584 PS104136 Reactor 1 Ethylene (kg/h) 40.4 35.7 35.6 35.6 35.7 24.5 Octene (kg/h) 1.7 1.5 1.9 1.4 2 0.6 Hydrogen (g/h) 1.04 0.7 0.6 0.6 0.7 0.4 Solvent (kg/h) 282 252.8 252.5 253.1 252.3 171 Reactor feed inlet 30 30 30 30 30 30 temperature (° C.) Reactor Temperature 163 162.3 162 161.7 162 162 (° C.) Catalyst (ppm) 0.1 0.11 0.12 0.12 0.14 0.12 Reactor 2 Ethylene (kg/h) 40.4 43.6 43.6 43.5 43.5 57 Octene (kg/h) 0 0 0 0 0 0 Hydrogen (g/h) 14.30 13.90 19.20 11.50 14.30 6.6 Solvent (kg/h) 102 132 131 131 131 222 Reactor feed inlet 30 30 30 30 30 30 temperature (° C.) Reactor Temperature 205 202 202 202 202 203 (° C.) Catalyst (ppm) 0.72 0.56 0.59 0.56 0.57 0.42

TABLE 3 Resin Properties Resin Inv. Ex. 1 Inv. Ex. 2 Inv. Ex. 3 Inv. Ex. 4 Inv. Ex. 5 Inv. Ex. 6 Material Name PS PS PS PS PS PS 101801 103550 103562 103574 103584 104136 Density (g/cm³) 0.9569 0.955 0.9575 0.9559 0.9555 0.9555 Rheology/Flow Properties Melt Index I₂ 7.66 7.21 7.29 4.54 7.17 8.1 (g/10 min) I₅ 21.9 13.2 23.5 I₂₁ 239 237 312 171 268 228 Melt Flow Ratio (I₂₁/I₂) 31.2 32.8 42.8 37.8 37.4 28.9 Stress Exponent 1.28 1.31 1.35 1.32 1.33 1.32 Shear Viscosity (η) at 10⁵ 5.9 6.3 4.8 6.2 5.6 6.9 s⁻¹ (240° C., Pa-s) 100/η at 10⁵ s⁻¹ (240° C.), 16.95 15.87 20.83 16.13 17.86 14.49 Processability Indicator Shear viscosity Ratio 66.4 60.9 79.6 84.5 70 51.78 (η100/η100000, 240° C.) GPC M_(n) 13088 16127 11001 16505 14020 23319 M_(w) 61162 59330 57976 68596 58484 63204 M_(z) 153222 144200 163371 187835 149424 148799 Polydispersity Index 4.67 3.68 5.27 4.16 4.17 2.71 (M_(w)/M_(n)) TREF CDBI(50) 71.1 80.3 72 79.5 78 78.9 CDBI(25) 59.5 70.6 62.4 68.1 68.7 67.2 Branch Frequency-FTIR (uncorrected for chain end —CH₃) Uncorrected SCB/1000C 1.7 1.4 2.1 1.5 1.8 0.9 Uncorrected comonomer 0.3 0.3 0.4 0.3 0.4 0.2 content (mol %) Comonomer ID 1-octene 1-octene 1-octene 1-octene 1-octene 1-octene Terminal 0.21 0.08 0.09 0.09 0.08 0.12 unsaturation/1000C Internal 0.09 0.16 0.13 0.14 0.14 0.11 unsaturation/1000C Side chain 0 0.01 0.01 0.00 0.01 0 unsaturation/1000C Total unsaturations/1000C 0.30 0.25 0.23 0.23 0.23 0.23 Comonomer mol % measured by ¹³C-NMR Hexyl+ branches 0.29 0.31 (>=4 C atoms), mol % DSC Primary Melting Peak (° C.) 129.77 129.72 129.71 130.0 129.46 131.5 Heat of Fusion (J/g) 217.6 214.2 218.8 216.4 215.7 215.6 Crystallinity (%) 75.04 73.88 75.44 74.63 74.37 74.33 Hexane Extractables (%) 0.33 Resin Comp. Ex. 1 Comp. Ex. 2 Comp. Ex. 3 Comp. Ex. 4 Comp. Ex. 5 Material Name PS 101778 PS 101787 PS 101793 J60-800-178 IG454-A Density (g/cm³) 0.9584 0.9585 0.9591 0.960 0.9540 Rheology/Flow Properties Melt Index I₂ (g/10 min) 7.18 7.51 8.56 8.52 9.00 I₅ I₂₁ 229 234 258 222 191 Melt Flow Ratio (I₂₁/I₂) 32 31.2 30.1 26.1 21.2 Stress Exponent 1.28 1.27 1.26 1.29 1.22 Shear Viscosity (η) at 10⁵ 5.8 5.7 6.9 7.9 s⁻¹ (240° C., Pa-s) 100/η at 10⁵ s⁻¹ (240° C.), 17.24 17.54 14.49 12.66 Processability Indicator Shear viscosity Ratio 54.6 47.9 (η100/η100000, 240° C.) GPC M_(n) 14526 13771 13469 17022 20519 M_(w) 64533 62612 59226 63567 59812 M_(z) 166380 157914 144926 181472 140168 Polydispersity Index 4.44 4.55 4.40 3.73 2.91 (M_(w)/M_(n)) TREF CDBI(50) 46.6 45.2 — 68.5 74.6 CDBI(25) 32.4 29.4 — 53.6 50.7 Branch Frequency- FTIR (uncorrected for chain end —CH₃) Uncorrected SCB/1000C 2.0 2 1.0 Uncorrected comonomer 0.4 0.4 <0.1 0.2 content (mol %) Comonomer ID 1-octene 1-octene 1-octene 1-butene 1-octene Terminal 0.16 0.12 0.14 0.17 0.50 unsaturation/1000C Internal 0.08 0.09 0.08 0.04 0 unsaturation/1000C Side chain 0.01 0.01 0.01 0 0.01 unsaturation/1000C Total unsaturations/1000C 0.25 0.22 0.23 0.21 0.51 Total unsaturations per 0.26 0.22 0.22 0.26 0.75 number average molecule Comonomer mol % measured by ¹³C-NMR Hexyl+ branches(<=4 — — — — — carbon atoms), mol % DSC Primary Melting Peak (° C.) 130.79 130.02 132.3 130.8 Heat of Fusion (J/g) 220.9 220.3 217.9 208.7 Crystallinity (%) 76.17 75.96 75.14 72.0 Hexane Extractables (%) 0.44 0.38 0.37

TABLE 4 Polyethylene Component Properties Resin Inv. Ex. 1 Inv. Ex. 2 Inv. Ex. 3 Inv. Ex. 4 Inv. Ex. 5 Inv. Ex. 6 Sample Name PS PS PS PS PS PS 101801 103550 103562 103574 103584 104136 Density (g/cm³) 0.9569 0.955 0.9575 0.9559 0.9555 0.9559 I₂ (g/10 min.) 7.66 7.21 7.29 4.54 7.17 8.2 Stress Exponent 1.28 1.31 1.35 1.32 1.33 1.31 MFR (I₂₁/I₂) 31.2 32.8 42.8 37.8 37.4 28.6 Mw/Mn 4.67 3.68 5.27 4.16 4.17 2.71 First Ethylene Polymer Weight fraction 0.5 0.48 0.48 0.47 0.47 0.32 Mw 107939 101355 109586 117645 105809 125184 I₂ (g/10 min.) 0.65 0.83 0.61 0.46 0.70 0.36 Density, d1 (g/cm³) 0.9421 0.9414 0.9395 0.9420 0.9402 0.9426 SCB1/1000C 0.66 0.8 0.93 0.59 0.88 0.48 Second Ethylene Polymer Weight fraction 0.5 0.52 0.52 0.53 0.53 0.68 Mw 15056 19854 12425 19110 15903 32391 I₂ (g/10 min.) 1433 486 3036 564 1157 72 Density, d2 (g/cm³) 0.9630 0.9615 0.9653 0.9621 0.9626 0.9593 SCB2/1000C 0.49 0.34 0.43 0.31 0.47 0.111 Estimated (d2-d1), g/cm³ 0.021 0.020 0.026 0.020 0.022 0.017 Estimated SCB1/SCB2 1.35 2.35 2.16 1.90 1.87 4.32 Resin Comp. Ex. 1 Comp. Ex. 2 Comp. Ex. 3 Sample Name PS 101788 PS 101787 PS 101793 Density (g/cm³) 0.9584 0.9585 0.9591 I₂ (g/10min.) 7.18 7.51 8.56 Stress Exponent 1.28 1.27 1.26 MFR (I₂₁/I₂) 32 31.2 30.1 Mw/Mn 4.44 4.55 4.4 First Ethylene Polymer Weight fraction 0.5 0.5 0.5 Mw 110512 108978 103442 I₂ (g/10 min.) 0.59 0.63 0.77 Density, dl (g/cm3) 0.9503 0.9504 0.9509 SCB1/1000C 0 0 0 Second Ethylene Polymer Weight fraction 0.5 0.5 0.5 Mw 14593 14618 14581 I₂ (g/10 min.) 1619 1608 1625 Density, d2 (g/cm³) 0.9552 0.9553 0.9553 SCB2/1000C 2.1 2.07 2.07 Estimated (d2-d1), g/cm³ 0.005 0.005 0.004 Estimated SCB1/SCB2 0.00 0.00 0.00

TABLE 5 Plaque Properties Resin Inv. Ex. 1 Inv. Ex. 2 Inv. Ex. 3 Inv. Ex. 4 Inv. Ex. 5 Environmental Stress Crack Resistance ESCR Cond. B at 100% (hrs.) 4 5 6 7 5 Flexural Properties (Plaques) Flex Secant Mod. 1% (MPa) 1352 1369 1460 1352 1308 Flex Sec Mod 1% (MPa) Dev. 58 37 33 76 51 Flex Secant Mod. 2% (MPa) 1135 1151 1245 1152 1114 Flex Sec Mod 2% (MPa) Dev. 35 18 17 52 34 Flexural Strength (MPa) 39.5 40.1 42.5 40.2 39.2 Flexural Strength Dev. (MPa) 0.4 0.4 0.5 1.1 0.7 Tensile Properties (Plaques) Elong. at Yield (%) 8 9 8 9 8 Elong. at Yield Dev. (%) 0 0 1 0 0 Yield Strength (MPa) 28.2 29.6 31 29.8 29.8 Yield Strength Dev. (MPa) 0.8 0.2 0.1 0.2 0.2 Ultimate Elong. (%) 1018 1033 491 1042 995 Ultimate Elong. Dev. (%) 39 36 523 105 32 Ultimate Strength (MPa) 18.8 18.8 20 23.4 19.1 Ultimate Strength Dev. (MPa) 0.8 0.9 4.7 4.4 0.6 Sec Mod 1% (MPa) 1702 1372 1644 1505 1531 Sec Mod 1% (MPa) Dev. 222 81 143 94 111 Sec Mod 2% (MPa) 1077 1022 1135 1069 1065 Sec Mod 2% (MPa) Dev. 67 47 57 37 19 Impact Properties (Plaques) Notched Izod Impact (ft-lb/in) 0.8 0.9 0.8 1 0.9 Notched Izod Impact (J/m) 42.72 48.06 42.72 53.4 48.06 Resin Comp. Ex. 1 Comp. Ex. 2 Comp. Ex. 3 Comp. Ex. 4 Comp. Ex. 5 Environmental Stress Crack Resistance ESCR Cond. B at 100% (hrs.) 1 1 1 5 5 Flexural Properties (Plaques) Flex Secant Mod. 1% (MPa) 1349 1374 1280 Flex Sec Mod 1% (MPa) Dev. 65 49 62 Flex Secant Mod. 2% (MPa) 1142 1149 1083 Flex Sec Mod 2% (MPa) Dev. 43 33 50 Flexural Strength (MPa) 40.4 40.6 37.9 Flexural Strength Dev. (MPa) 0.7 0.6 1 Tensile Properties (Plaques) Elong. at Yield (%) 9 8 10 Elong. at Yield Dev. (%) 0 1 1 Yield Strength (MPa) 29 29.1 27.9 Yield Strength Dev. (MPa) 0.4 0.3 0.5 Ultimate Elong. (%) 450 11 1433 (very brittle failure) Ultimate Elong. Dev. (%) 165 1 200 Ultimate Strength (MPa) 14.8 29.1 23.9 (very brittle failure) Ultimate Strength Dev. (MPa) 0.9 0.3 3.7 Sec Mod 1% (MPa) 1728 1405 1263 Sec Mod 1% (MPa) Dev. 292 359 404 Sec Mod 2% (MPa) 1106 1038 904 Sec Mod 2% (MPa) Dev. 69 102 116 Impact Properties (Plaques) Notched Izod Impact (ft-lb/in) 0.6 0.6 1 Notched Izod Impact (J/m) 32.04 32.04 53.4

TABLE 6 Dimensional Stability Resin Inv. Ex. 1 Inv. Ex. 2 Inv. Ex 3 Inv. Ex. 4 Inv. Ex. 5 Inv. Ex. 6 TD shrinkage, IM disk, 48 hr. 1.67 1.87 1.93 1.71 1.79 1.84 MD shrinkage, IM disk, 48 hr. 1.62 1.72 1.93 1.77 1.77 1.89 (TD shrinkage-MD shrinkage), IM disk, 48 hr. 0.05 0.15 0 −0.06 0.02 −0.05 TD/MD shrinkage ratio, isotropy indicator, IM disk, 48 hr. 1.03 1.09 1.00 0.97 1.09 0.97 Resin Comp. Ex. 4 Comp. Ex. 5 Com. Ex. 6 Comp. Ex. 7 Comp. Ex.8 TD shrinkage, IM disk, 48 hr. 1.82 1.69 1.79 1.77 1.89 MD shrinkage, IM disk, 48 hr. 1.68 1.31 1.98 2.17 2.17 (TD shrinkage-MD shrinkage), 0.14 0.38 −0.19 −0.40 −0.28 IM disk, 48 hr. TD/MD shrinkage ratio, isotropy 1.08 1.29 0.90 0.82 0.87 indicator, IM disk, 48 hr.

As can be seen from the data provided in Tables 3-6 and FIGS. 1-3, the inventive polyethylene compositions have very good dimensional stability, are easy to process (e.g., have good injectability when making an injection molded part), show good organoleptic properties and impact resistance and have useful ESCR for applications such as water bottle closures. For example, FIG. 1 shows that relative to comparative examples 1, 2, 4 (J60-800-178) and 5 (IG454-A), the inventive compositions 1-5 have an improved balance of processability and ESCR. Also, as shown in FIG. 2, the inventive compositions 1-5 have a better balance of processability and impact strength when compared to comparative resins 1, 2, 4 (J60-800-178) and 5 (IG454-A). The processability comparison is made on the basis of a “processability indicator” which in the present invention is defined as 100/η at 10⁵ s⁻¹ (240° C.), where η is the Shear Viscosity (η) at 10⁵ s⁻¹ (240° C., Pa-s) as defined above.

FIG. 3 shows that the inventive compositions 1 and 2 have a better dimensional stability (the TD/MD shrinkage isotropy indicator) than a polypropylene homopolymer having a melt flow rate of 35 g/10 min (tested at 230° C. under 2.16 kg). Inventive compositions 1 and 2 have comparable or better dimensional stability than comparative examples 4 (J60-800-178) and 5 (IG454-A).

Table 6 shows that inventive polyethylene compositions 1-6 generally have better dimensional stability than comparative resins 4-8. Compare, for example, inv. compositions 1, 2, 3, 4, 5 and 6 which have a TD shrinkage—MD shrinkage of 0.05, 0.15, 0, −0.06, 0.02, and −0.05 respectively with comp. resins 4, 5, 6, 7, and 8 which have a TD shrinkage—MD shrinkage of 0.14, 0.38, −0.19, −0.40, −0.28 respectively. Also compare the TD/MD shrinkage ratio (the indicator of isotropy) for inventive compositions 1, 2, 3, 4, 5 and 6 at 1.03, 1.09, 1, 0.97, 1.09 and 0.97 respectively which are all fairly close to 1, with the TD/MD shrinkage ratio (the indicator of isotropy) for comp. compositions 4, 5, 6, 7, and 8 which are 1.08, 1.29, 0.90, 0.82, and 0.87, respectively.

FIGS. 4A and 4B compare the composition distribution breadth index CDBI(50) of inventive example 1 with comparative example 2 as determined by temperature elution rising fractionation (TREF). Comparative example 2 shows three peaks in the TREF profile and has a CDBI(50) of 45.2 weight percent (wt %). Inventive example 1 shows a single dominant peak in the TREF profile and has a CDBI(50) of greater than 70 wt %. Hence, inventive example 1 has a more uniform composition distribution, which is thought to increase polymer toughness (e.g., impact resistance).

Further, inventive resin 1, indeed all the inventive compositions have relatively high CDBI(25) values (see Table 3). Compare for example the TREF analysis of inventive resin 1 (CDBI(25)=59.5%) with comparative resin 2 (CDBI(25)=29.4%) as shown in FIGS. 4A and 4B. Also see the data in Table 3 where inventive resins 1-6 all have a CDBI(25) of greater than 59% by weight, while comparative resins 1, 2, 4 and 5 all have CDBI(25) values of less than about 54% by weight. Indeed, comparative resins 1 and 2 have CDBI(25) values of less than 35% by weight.

The polyethylene compositions of the present invention can be used in drinkable water, juice, hot fill applications or other non-pressurized caps and closures applications.

The present invention has been described with reference to certain details of particular embodiments thereof. It is not intended that such details be regarded as limitations upon the scope of the invention except insofar as and to the extent that they are included in the accompanying claims. 

What is claimed is:
 1. A closure for bottles, the closure comprising a polyethylene composition, the polyethylene composition comprising: (1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and (2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index 1₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs; and wherein the closure is a hinged closure.
 2. The closure of claim 1 wherein the polyethylene composition has a TD/MD shrinkage ratio of from about 0.90 to about 1.15 when measured according to the Dimensional Stability Test (DST).
 3. The closure of claim 1 wherein the polyethylene composition has an ESCR Condition B (100% IGEPAL) of from about 3.5 to about 15 hrs.
 4. The closure of claim 1 wherein the polyethylene composition has a melt index I₂, of greater than 5.0 to less than 20 g/10 min.
 5. The closure of claim 1 wherein the first and second ethylene copolymers are made by polymerizing ethylene and an alpha olefin in the presence of a single site catalyst.
 6. The closure of claim 1 wherein the density of the second ethylene copolymer is less than 0.030 g/cm³ higher than the density of the first ethylene copolymer.
 7. The closure of claim 1 wherein the first ethylene copolymer has a melt index I₂, of from 0.1 to 3.0 g/10 min.
 8. The closure of claim 1 wherein the second ethylene copolymer has a melt index I₂, of from 100 to 5000 g/10 min.
 9. The closure of claim 1 wherein the polyethylene composition has a melt index I₂, of from 6 to 12 g/10 min.
 10. The closure of claim 1 wherein the polyethylene composition has a bimodal molecular weight distribution as determined by gel permeation chromatography.
 11. The closure of claim 1 wherein the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is at least 1.5.
 12. The closure of claim 1 wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 3.5 to
 6. 13. The closure of claim 1 wherein the first ethylene copolymer has a density of from 0.936 to 0.952 g/cm³.
 14. The closure of claim 1 wherein the second ethylene copolymer has a density of less than 0.965 g/cm³.
 15. The closure of claim 1 wherein the polyethylene composition has a density of from 0.952 to 0.960 g/cm³.
 16. The closure of claim 1 wherein the polyethylene composition has no long chain branching.
 17. The closure of claim 1 wherein the first and second ethylene copolymers have a M_(w)/M_(n) of less than 2.5.
 18. The closure of claim 1 wherein the polyethylene composition has a composition distribution breadth index (CDBI(50)) of greater than about 65 wt %.
 19. The closure of claim 1 wherein the first and second ethylene copolymers each have a composition distribution breadth index (CDBI(50)) of greater than about 65 wt %.
 20. The closure of claim 1 wherein the polyethylene composition comprises: from about 25 to about 60 wt % of the first ethylene copolymer; and from about 75 to about 40 wt % of the second ethylene copolymer.
 21. The closure of claim 1 wherein the polyethylene composition has a comonomer content of less than about 0.5 mol % as determined by ¹³C NMR.
 22. The closure of claim 1 wherein the polyethylene composition further comprises a nucleating agent or a combination of nucleating agents.
 23. The closure of claim 1 wherein the first and second ethylene copolymers are copolymers of ethylene and 1-octene.
 24. The closure of claim 1 wherein the closure is made by compression molding or injection molding.
 25. The closure of claim 1 wherein the closure is a screw cap.
 26. The closure of claim 1 wherein the polyethylene composition is prepared by contacting ethylene and an alpha-olefin with a single site polymerization catalyst under solution polymerization conditions in a least two polymerization reactors.
 27. A process for preparing a closure for bottles wherein the process comprises at least one compression molding or injection molding step and wherein the closure comprises a polyethylene composition, the polyethylene composition comprising: (1) about 10 to about 70 wt % of a first ethylene copolymer having a melt index I₂, of from 0.1 to 10 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density of from 0.930 to 0.960 g/cm³; and (2) about 90 to about 30 wt % of a second ethylene copolymer having a melt index I₂, of from 50 to 10,000 g/10 min; a molecular weight distribution M_(w)/M_(n), of less than 3.0; and a density higher than the density of the first ethylene copolymer, but less than 0.966 g/cm³; wherein the density of the second ethylene copolymer is less than 0.037 g/cm³ higher than the density of the first ethylene copolymer; the ratio (SCB1/SCB2) of the number of short chain branches per thousand carbon atoms in the first ethylene copolymer (SCB1) to the number of short chain branches per thousand carbon atoms in the second ethylene copolymer (SCB2) is greater than 1.0; and wherein the polyethylene composition has a molecular weight distribution M_(w)/M_(n), of from 2 to 7; a density of at least 0.950 g/cm³; a high load melt index I₂₁, of from 150 to 400 g/10 min; a Z-average molecular weight M_(Z), of less than about 300,000; a melt flow ratio I₂₁/I₂, of from 22 to 50; a stress exponent of less than 1.40; and an ESCR Condition B (100% IGEPAL) of at least about 3.5 hrs; and wherein the closure is a hinged closure. 